JP5181439B2 - Non-oriented electrical steel sheet - Google Patents
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- JP5181439B2 JP5181439B2 JP2006202681A JP2006202681A JP5181439B2 JP 5181439 B2 JP5181439 B2 JP 5181439B2 JP 2006202681 A JP2006202681 A JP 2006202681A JP 2006202681 A JP2006202681 A JP 2006202681A JP 5181439 B2 JP5181439 B2 JP 5181439B2
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- 229910000565 Non-oriented electrical steel Inorganic materials 0.000 title claims description 16
- 229910000831 Steel Inorganic materials 0.000 claims description 39
- 239000010959 steel Substances 0.000 claims description 39
- 229910052757 nitrogen Inorganic materials 0.000 claims description 11
- 229910052748 manganese Inorganic materials 0.000 claims description 8
- 229910052698 phosphorus Inorganic materials 0.000 claims description 7
- 239000012535 impurity Substances 0.000 claims description 6
- 229910052717 sulfur Inorganic materials 0.000 claims description 5
- 229910052799 carbon Inorganic materials 0.000 claims description 4
- 239000000203 mixture Substances 0.000 claims description 4
- 229910052802 copper Inorganic materials 0.000 claims description 3
- 229910052759 nickel Inorganic materials 0.000 claims description 3
- 229910052804 chromium Inorganic materials 0.000 claims description 2
- 229910052718 tin Inorganic materials 0.000 claims description 2
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 18
- 239000002344 surface layer Substances 0.000 description 18
- 238000000137 annealing Methods 0.000 description 17
- 238000005121 nitriding Methods 0.000 description 12
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 10
- 229910052742 iron Inorganic materials 0.000 description 7
- 238000000034 method Methods 0.000 description 7
- 238000005255 carburizing Methods 0.000 description 6
- 239000000463 material Substances 0.000 description 6
- 238000005097 cold rolling Methods 0.000 description 5
- 238000005098 hot rolling Methods 0.000 description 5
- 238000004080 punching Methods 0.000 description 5
- 230000000977 initiatory effect Effects 0.000 description 4
- 238000004519 manufacturing process Methods 0.000 description 4
- 238000004804 winding Methods 0.000 description 4
- 229910000976 Electrical steel Inorganic materials 0.000 description 3
- 238000009661 fatigue test Methods 0.000 description 3
- 230000004907 flux Effects 0.000 description 3
- 239000012299 nitrogen atmosphere Substances 0.000 description 3
- 238000005728 strengthening Methods 0.000 description 3
- 238000005253 cladding Methods 0.000 description 2
- 229910052739 hydrogen Inorganic materials 0.000 description 2
- 238000005259 measurement Methods 0.000 description 2
- 238000005554 pickling Methods 0.000 description 2
- 239000002244 precipitate Substances 0.000 description 2
- 238000001556 precipitation Methods 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- 230000001133 acceleration Effects 0.000 description 1
- 239000012298 atmosphere Substances 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 238000000605 extraction Methods 0.000 description 1
- 230000002349 favourable effect Effects 0.000 description 1
- 239000012467 final product Substances 0.000 description 1
- 239000004615 ingredient Substances 0.000 description 1
- 150000001247 metal acetylides Chemical class 0.000 description 1
- 229910052758 niobium Inorganic materials 0.000 description 1
- 230000008520 organization Effects 0.000 description 1
- 238000007747 plating Methods 0.000 description 1
- 150000003568 thioethers Chemical class 0.000 description 1
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Description
本発明は、無方向性電磁鋼板、特に、疲労特性に優れた無方向性電磁鋼板に関する。 The present invention relates to a non-oriented electrical steel sheet, and more particularly to a non-oriented electrical steel sheet having excellent fatigue characteristics.
電気自動車用モータのような、車の加減速にともない回転数が大きく変動するモータにおいては、そのロータ用材料である電磁鋼板に対して、磁気特性と疲労特性に優れていることが要求されている。このような特性は、電気自動車用モータだけではなく、インバータにより可変速運転が行われる高効率エアコン用モータにおいても要求されている。 In motors such as motors for electric vehicles, whose rotational speed fluctuates greatly with the acceleration / deceleration of the vehicle, it is required that the magnetic steel sheet, which is the material for the rotor, has excellent magnetic and fatigue characteristics. Yes. Such characteristics are required not only for electric vehicle motors, but also for high-efficiency air conditioner motors that are operated at variable speeds by inverters.
こうした磁気特性と機械特性を兼ね備えた無方向性電磁鋼板として、例えば、特許文献1には、Nb添加により析出強化された高張力無方向性電磁鋼板が開示されている。また、特許文献2には、磁石内蔵タイプのロータのブリッジ部に板厚減少部を塑性加工により形成し、その部分を窒化処理により高強度化して高速回転を可能する電磁鋼板ロータの製造方法が開示されている。
しかしながら、特許文献1に記載の高張力無方向性電磁鋼板では、W10/1000が100W/kg程度で、これはW10/400に換算するとほぼ40W/kgぐらいで十分に低い鉄損が得られない。特許文献2に記載の方法では、ブリッジ部の一部を塑性加工し、その部分に窒化処理を施す必要があり、ロータの生産性を著しく阻害する。
However, the high-tensile non-oriented electrical steel sheet described in Patent Document 1, W 10/1000 is of about 100W / kg, which is sufficiently low iron loss at around approximately 40W / kg in terms of W 10/400 is obtained I can't. In the method described in
本発明は、ロータの作製上の問題を引き起こすことなく、磁気特性と疲労特性に優れた無方向性電磁鋼板を提供することを目的とする。 An object of the present invention is to provide a non-oriented electrical steel sheet having excellent magnetic characteristics and fatigue characteristics without causing problems in the production of a rotor.
本発明者らが、磁気特性と疲労特性が両立するような無方向性電磁鋼板について検討したところ、以下のことを見出した。
(1)鋼板表層部のみを高強度化し、かつ板厚中心部のビッカース硬度の1.3倍以上の硬度を有する領域を鋼板表面から板厚中心部に向かって5〜50μmの範囲に形成させることが効果的である。
When the present inventors examined the non-oriented electrical steel sheet which makes a magnetic characteristic and a fatigue characteristic compatible, the following thing was discovered.
(1) Strengthening only the surface layer of the steel sheet and forming a region having a hardness of 1.3 times or more of the Vickers hardness of the center of the thickness in the range of 5 to 50 μm from the steel sheet surface toward the center of the thickness It is effective.
本発明は、このような知見に基づきなされたもので、質量%で、Si:0.5〜4%、Mn:0.05〜5%、Al:0.32〜3%、残部Feおよび不可避的不純物からなり、かつ板厚中心部のビッカース硬度の1.3倍以上の硬度を有する領域が鋼板表面から板厚中心部に向かって5〜50μmの範囲に及ぶ無方向性電磁鋼板を提供する。 The present invention has been made on the basis of such knowledge, and in mass%, Si: 0.5 to 4 %, Mn: 0.05 to 5%, Al: 0.32 to 3 %, the balance Fe and inevitable impurities, and Provided is a non-oriented electrical steel sheet in which a region having a hardness of 1.3 times or more of the Vickers hardness at the center of the plate thickness extends from 5 to 50 μm from the steel plate surface toward the center of the plate thickness.
例えば、板厚中心部の組成が、質量%で、C:0.008%以下、Si:0.5〜4%、Mn:0.05〜5%、P:0.2%以下、S:0.02%以下、Al:0.32〜3%、N:0.008%以下、残部Feおよび不可避的不純物からなり、かつ鋼板表面から板厚中心部に向かって5〜50μmの領域のN量が0.01%以上である無方向性電磁鋼板や、板厚中心部の組成が、質量%で、C:0.008%以下、Si:0.5〜4%、Mn:0.05〜5%、P:0.2%以下、S:0.02%以下、Al:0.32〜3%、N:0.008%以下を含有し、残部Feおよび不可避的不純物からなり、かつ鋼板表面から板厚中心部に向かって5〜50μmの領域のC量が0.01%以上である無方向性電磁鋼板を挙げることができる。 For example, the composition at the center of the plate thickness is mass%, C: 0.008% or less, Si: 0.5 to 4 %, Mn: 0.05 to 5%, P: 0.2% or less, S: 0.02% or less, Al: 0.32 to 3 %, N: 0.008% or less, balance Fe and unavoidable impurities, non-oriented electrical steel sheet in which the N content in the region of 5 to 50 μm from the steel sheet surface toward the thickness center is 0.01% or more, Composition at the center of the plate thickness is% by mass: C: 0.008% or less, Si: 0.5-4 %, Mn: 0.05-5%, P: 0.2% or less, S: 0.02% or less, Al: 0.32-3 % , N: 0.008% or less, and a balance of Fe and unavoidable impurities, and C of 5~50μm region from the steel sheet surface toward the thickness center portion is a non-oriented electrical steel sheet is 0.01% or more Can be mentioned.
さらに、質量%で、Sn:0.002〜0.05%、Sb:0.001〜0.05%、Ni:0.01〜5%、Cu:0.01〜2%、Co:0.05〜5%、Cr:0.1〜5%のうちから選ばれた少なくとも1種の元素を含有させることができる。 Furthermore, in mass%, Sn: 0.002-0.05%, Sb: 0.001-0.05%, Ni: 0.01-5%, Cu: 0.01-2%, Co: 0.05-5%, Cr: 0.1-5% At least one selected element can be contained.
本発明により、ロータの作製上の問題を引き起こすことなく、B50が1.60T以上、W10/400が23W/kg以下で、疲労限が330MPa以上の無方向性電磁鋼板を製造できるようになった。 According to the present invention, a non-oriented electrical steel sheet having a B50 of 1.60 T or more, a W 10/400 of 23 W / kg or less, and a fatigue limit of 330 MPa or more can be produced without causing problems in the production of the rotor. .
以下に、本発明の詳細を説明する。(なお、成分に関する「%」表示は、特に断らない限り質量%を意味するものとする。)
電磁鋼板の疲労特性を向上させるためには、疲労亀裂のイニシエーションを抑制することが重要である。そこでまず、電磁鋼板の疲労亀裂のイニシエーションサイトについて調査を行った。その結果、打ち抜き時に生じるバリ近傍から疲労亀裂が発生していることが明らかとなった。このことから、本発明者らは、バリの大きさを低減するとともに、バリ近傍、すなわち鋼板表層部を高強度化すれば、板厚中心部付近を高強度化する必要はなく、磁気特性に好ましい組織にすることが可能であるとの考えに到った。
Details of the present invention will be described below. (Note that “%” in relation to ingredients means mass% unless otherwise specified.)
In order to improve the fatigue characteristics of the electrical steel sheet, it is important to suppress the initiation of fatigue cracks. First of all, we investigated the initiation site of fatigue cracks in electrical steel sheets. As a result, it became clear that fatigue cracks occurred from the vicinity of burrs generated during punching. From this, the present inventors reduced the size of burrs and increased the strength of the vicinity of the burrs, i.e., the surface layer of the steel sheet. It came to the idea that it could be a favorable organization.
そこで、まず、鋼板表層部の高強度化による疲労限向上について、以下の検討を行った。Si:2.8%、Mn:0.18%、P:0.01%、Al:0.30%、N:0.0015%とした鋼を実験室で溶解し、熱間圧延後、1000℃×30sの熱延板焼鈍を行い、板厚0.35mmまで冷間圧延を行い、引き続き10%H2-90%N2雰囲気にて10s間仕上焼鈍を行った後、雰囲気のN2分圧を0〜100%に変化させて850℃×3hrの焼鈍を行い、窒化処理により表層部の高強度化を図って、疲労試験を行った。疲労試験は、仕上焼鈍後と窒化処理後の鋼板より平行部の幅5mm、長さ150mmのサンプルを打ち抜きにより作製し、応力比0.1、周波数20Hzの部分片振り(引張り-引張り)で行い、繰り返し数107回において破壊が生じない応力振幅、すなわち疲労限を求めた。 Therefore, first, the following examination was conducted to improve the fatigue limit by increasing the strength of the steel sheet surface layer. Steel with Si: 2.8%, Mn: 0.18%, P: 0.01%, Al: 0.30%, N: 0.0015% was melted in the laboratory, hot-rolled, and then annealed at 1000 ° C for 30s. , After cold rolling to a plate thickness of 0.35 mm, followed by finish annealing for 10 s in a 10% H 2 -90% N 2 atmosphere, the N 2 partial pressure of the atmosphere was changed to 0 to 100% and 850 A fatigue test was performed by annealing at 3 ° C. for 3 hours and increasing the strength of the surface layer by nitriding. The fatigue test was performed by punching a sample with a width of 5 mm and a length of 150 mm from the steel sheet after finish annealing and nitriding, and performing it by partial swinging (tensile-tensile) with a stress ratio of 0.1 and a frequency of 20 Hz. The stress amplitude at which fracture does not occur in several 10 7 times, that is, the fatigue limit, was obtained.
図1に、鋼板表面から5μmの領域でのビッカース硬度HVSと板厚中心部のビッカース硬度HVCの比(HVS/HVC)と疲労限の関係を示す。HVS/HVCが1.3以上となった場合に330MPa以上の疲労限が得られることがわかる。この原因を調査するため疲労亀裂のイニシエーションサイトであるバリの観察を行ったところ、窒化処理により表層部の強度を高めた材料ではバリ高さが小さくなっており、このバリ高さの減少とイニシエーションサイト近傍の高強度化により疲労亀裂の発生が抑制されたものと考えられる。
FIG. 1 shows the relationship between the fatigue limit and the ratio (HV S / HV C ) between the Vickers hardness HV S and the Vickers hardness HV C at the thickness center in the
次に、表面からの強度を向上させた領域の深さと疲労限との関係を調査するため、以下の検討を行った。Si:2.8%、Mn:0.18%、P:0.01%、Al:0.50%、N:0.0020%とした鋼を実験室で溶解し、熱間圧延後、1000℃×30sの熱延板焼鈍を行い、板厚0.35mmまで冷間圧延を行い、引き続き10%H2-90%N2雰囲気にて10s間仕上焼鈍を行った後、100%N2雰囲気にて850℃×0〜10hrの焼鈍を行い、窒化処理により表層部の高強度化を図って、上記の疲労試験を行って疲労限を求めた。また、25cmエプスタイン試験片を用いてW10/400を測定した。 Next, in order to investigate the relationship between the depth of the region where the strength from the surface was improved and the fatigue limit, the following examination was performed. Steel with Si: 2.8%, Mn: 0.18%, P: 0.01%, Al: 0.50%, N: 0.0020% was melted in the laboratory, and after hot rolling, hot-rolled sheet annealing at 1000 ° C x 30s was performed. Then, cold-roll to a sheet thickness of 0.35 mm, and then finish annealing for 10 s in a 10% H 2 -90% N 2 atmosphere, followed by annealing at 850 ° C. × 0 to 10 hours in a 100% N 2 atmosphere The surface layer was strengthened by nitriding, and the fatigue test was conducted to determine the fatigue limit. In addition, W 10/400 was measured using a 25 cm Epstein test piece.
図2に、板厚中心部のビッカース硬度の1.3倍以上の硬度を有する領域の鋼板表面からの範囲と疲労限および鉄損との関係を示す。板厚中心部のビッカース硬度の1.3倍以上の硬度を有する領域の鋼板表面からの範囲が5μm未満では、疲労限を向上させる効果が小さいことがわかる。一方、この領域の鋼板表面からの範囲が50μmを超えると鉄損が増大する。以上のことから、板厚中心部のビッカース硬度の1.3倍以上の硬度を有する領域の範囲は鋼板表面から板厚中心部に向かって5〜50μmである必要がある。 FIG. 2 shows the relationship between the range from the steel sheet surface in a region having a hardness of 1.3 times or more of the Vickers hardness at the center of the plate thickness, the fatigue limit, and the iron loss. It can be seen that the effect of improving the fatigue limit is small when the range from the steel plate surface in the region having a hardness of 1.3 times or more of the Vickers hardness at the center of the plate thickness is less than 5 μm. On the other hand, when the range from the steel sheet surface in this region exceeds 50 μm, the iron loss increases. From the above, the range of the region having a hardness of 1.3 times or more of the Vickers hardness at the center of the plate thickness needs to be 5 to 50 μm from the steel plate surface toward the center of the plate thickness.
表層部の硬化された領域の窒素量を調査するため、鋼板表面より所定の領域範囲まで電解抽出を行い、析出物としての窒素量と固溶している窒素量を求め、両者を合わせたトータルの窒素量を求めた。その結果、硬度と窒素量には良い相関が認められ、HVS/HVC≧1.3の領域の窒素量は0.01%以上であることが明らかとなり、0.02%以上にすることにより疲労強度がさらに向上することが明らかとなった。なお、窒化処理は打ち抜き加工後に行ってもよいが、バリ高さの減少の観点からは打ち抜き前に施すことが好ましい。 In order to investigate the amount of nitrogen in the hardened region of the surface layer part, electrolytic extraction was performed from the steel sheet surface to a predetermined region range, the amount of nitrogen as precipitates and the amount of solid solution were obtained, and the total of both The amount of nitrogen was determined. As a result, a good correlation was found between hardness and nitrogen content, and it became clear that the nitrogen content in the region of HV S / HV C ≧ 1.3 was 0.01% or more, and fatigue strength was further improved by making it 0.02% or more. It became clear to do. The nitriding treatment may be performed after punching, but is preferably performed before punching from the viewpoint of reducing the burr height.
このような表層部を高強度化する手法としては浸炭処理も有効である。この場合も高強度化される領域のC量を0.01%以上、より好ましくは0.02％以上とする。 Carburizing treatment is also effective as a method for increasing the strength of the surface layer. Also in this case, the amount of C in the region to be strengthened is 0.01% or more, more preferably 0.02% or more.
窒化処理や浸炭処理を施す前の電磁鋼板の成分、すなわち鋼板の板厚中心部の値で代表される成分の含有量は、次のように限定する必要がある。 It is necessary to limit the content of the component of the electrical steel sheet before the nitriding treatment or carburizing treatment, that is, the component represented by the value of the center portion of the steel plate thickness as follows.
Si:鋼板の固有抵抗を上げ、鉄損を低下させるのに有効な元素であるが、4%を超えると飽和磁束密度の低下にともない低磁場における磁束密度を低下させるので、Si量は4%以下とし、好ましくは0.5%以上とする。 Si: It is an element effective for increasing the specific resistance of steel sheets and reducing iron loss.However, if it exceeds 4%, the magnetic flux density in a low magnetic field is reduced as the saturation magnetic flux density is reduced. Or less, preferably 0.5% or more.
Mn:熱間圧延時の赤熱脆性を防止するために0.05%以上にする必要があるが、5%を超えると磁束密度が低下するので、Mn量は0.05〜5%とする。 Mn: In order to prevent red hot brittleness during hot rolling, it is necessary to be 0.05% or more. However, if it exceeds 5%, the magnetic flux density decreases, so the Mn content is 0.05-5%.
Al:Siと同様に、鋼板の固有抵抗を上げ、鉄損を低下させるのに有効な元素であるが、3%を超えると飽和磁束密度の低下にともない低磁場における磁束密度を低下させるので、Al量は3%以下とし、好ましくは0.2%以上とする。 Like Al: Si, it is an element that is effective in increasing the specific resistance of the steel sheet and lowering iron loss. The Al content is 3% or less, preferably 0.2% or more.
残部はFeおよび不可避的不純物である。 The balance is Fe and inevitable impurities.
また、C、P、S、Nの含有量は、次のようにすることが好ましい。 Further, the contents of C, P, S, and N are preferably as follows.
C:炭化物を形成し、磁気特性を劣化させるため、C量は0.008%以下とすることが好ましい。 C: In order to form carbides and deteriorate magnetic properties, the C content is preferably 0.008% or less.
P:鋼板の打抜き加工性を改善するために有効な元素であるが、0.2%を超えると鋼板が脆化するので、P量は0.2%以下とし、好ましくは0.005%以上とする。 P: An element effective for improving the punching workability of the steel sheet, but if it exceeds 0.2%, the steel sheet becomes brittle, so the P content is 0.2% or less, preferably 0.005% or more.
S:硫化物を形成し、磁気特性を劣化させるため、S量は0.02%以下とする。 S: The amount of S is set to 0.02% or less in order to form sulfides and deteriorate magnetic properties.
N:AlNとして析出し、鉄損を増大させるので、N量は0.008%以下とする。 N: precipitates as AlN and increases iron loss, so the N content is 0.008% or less.
さらに、これらの元素に加え、磁気特性向上のために、Sn:0.002〜0.05%、Sb:0.001〜0.05%、Ni:0.01〜5%、Cu:0.01〜2%、Co:0.05〜5%、Cr:0.1〜5%のうちから選ばれた少なくとも1種の元素を含有させることが好ましい。 In addition to these elements, in order to improve magnetic properties, Sn: 0.002 to 0.05%, Sb: 0.001 to 0.05%, Ni: 0.01 to 5%, Cu: 0.01 to 2%, Co: 0.05 to 5%, It is preferable to contain at least one element selected from Cr: 0.1 to 5%.
本発明の無方向性電磁鋼板においては、成分および鋼板表層部の硬度が所定の範囲内にあれば、鋼板表層部の硬度調整以外は、通常の製造方法を適用できる。すなわち、転炉で吹練した溶鋼を脱ガス処理して所定の成分に調整し、鋳造、熱間圧延を行い、次いで、必要に応じて熱延板焼鈍を行い、一回の冷間圧延、もしくは中間焼鈍をはさんだ2回以上の冷間圧延により所定の板厚とした後に、仕上焼鈍を行う。仕上焼鈍後、窒化処理や浸炭処理を施すことにより、表層部のみを高強度化することが可能である。なお、窒化処理や浸炭処理は熱延板焼鈍の段階で行っても構わない。 In the non-oriented electrical steel sheet of the present invention, as long as the hardness of the component and the steel sheet surface layer part is within a predetermined range, a normal manufacturing method can be applied except for the hardness adjustment of the steel sheet surface layer part. That is, the molten steel blown in the converter is degassed and adjusted to a predetermined component, cast, hot rolled, then hot-rolled sheet annealed as necessary, one cold rolling, Alternatively, finish annealing is performed after a predetermined thickness is obtained by cold rolling at least twice with intermediate annealing. It is possible to increase the strength of only the surface layer portion by performing nitriding treatment or carburizing treatment after finish annealing. In addition, you may perform a nitriding process and a carburizing process in the stage of hot-rolled sheet annealing.
また、スラブ段階で表層部に高強度材をクラッドすることにより、最終製品の表層部の硬度を高めることも可能である。表層へのクラッド材として、例えば、Ti、Nb等の析出強化を活用した材料やSi、Mn、Al等の固溶強化を活用した材料を用いることが可能である。 It is also possible to increase the hardness of the surface layer portion of the final product by cladding a high strength material on the surface layer portion in the slab stage. As the cladding material for the surface layer, for example, a material utilizing precipitation strengthening such as Ti or Nb or a material utilizing solid solution strengthening such as Si, Mn or Al can be used.
さらに、仕上焼鈍板にNiメッキを施し、拡散処理を行うことにより鋼板の表層部のＮｉ量を高めることにより表層部の強度を高めることも可能である。 Furthermore, it is also possible to increase the strength of the surface layer portion by increasing the amount of Ni in the surface layer portion of the steel sheet by applying Ni plating to the finish annealing plate and performing a diffusion treatment.
転炉で吹練した後に脱ガス処理を行って表1に示す成分に調整した鋼No.A〜Kをスラブに鋳造後、スラブを1100℃で1時間加熱した後、板厚2.0mmまで熱間圧延を行った。熱間圧延の仕上温度は800℃、巻取温度は610℃とし、巻取り後は、酸洗し、1000℃×30sの熱延板焼鈍を施した。その後、板厚0.35mmまで冷間圧延を行い、表2に示す仕上焼鈍温度で30秒間の仕上焼鈍を行い、さらに表2に示す窒化処理条件で窒化処理を施して鋼板No.1〜17を作製した。そして、板厚方向のビッカース硬度(荷重10g)、N量の測定や、上記の方法で磁気特性(W10/400、B50)および疲労限の測定を行った。 After steel No. A to K, which was degassed and then adjusted to the components shown in Table 1 after casting in a converter, was cast into a slab, the slab was heated at 1100 ° C for 1 hour, and then heated to a thickness of 2.0 mm. Hot rolling was performed. The finishing temperature of hot rolling was 800 ° C. and the winding temperature was 610 ° C. After winding, pickling was performed, and hot rolled sheet annealing was performed at 1000 ° C. × 30 s. Thereafter, cold rolling to a sheet thickness of 0.35 mm, finish annealing for 30 seconds at the finish annealing temperature shown in Table 2, and further nitriding under the nitriding conditions shown in Table 2 to obtain steel plates Nos. 1 to 17 Produced. Then, measurement of Vickers hardness (load 10 g) and N amount in the plate thickness direction, and magnetic characteristics (W 10/400 , B50) and fatigue limit were performed by the above-described methods.
結果を表2に示す。成分および鋼板表層部の硬度を本発明の範囲内に制御した発明例である鋼板No.3〜6、9〜14では、B50が1.60T以上、W10/400が23W/kg以下で、330MPa以上の疲労限が得られることがわかる。 The results are shown in Table 2. In steel plate Nos. 3 to 6 and 9 to 14 which are invention examples in which the hardness of the component and the steel sheet surface layer portion is controlled within the scope of the present invention, B50 is 1.60 T or more, W 10/400 is 23 W / kg or less, 330 MPa It can be seen that the above fatigue limit can be obtained.
転炉で吹練した後に脱ガス処理を行って表3に示す成分に調整した鋼No.Lをスラブに鋳造後、スラブを1100℃で1時間加熱した後、板厚2.3mmまで熱間圧延を行った。熱間圧延の仕上温度は800℃、巻取温度は610℃とし、巻取り後は、酸洗し、1000℃×30sの熱延板焼鈍を施した。その後、板厚0.35mmまで冷間圧延を行い、表4に示す仕上焼鈍温度で30秒間の仕上焼鈍を行い、さらに表4に示す浸炭処理条件で浸炭処理を施して鋼板No.18〜24を作製した。そして、板厚方向のビッカース硬度(荷重10g)、C量の測定や、上記の方法で磁気特性(W10/400、B50)および疲労限の測定を行った。 After steel No.L, which was degassed in a converter and degassed and adjusted to the components shown in Table 3, was cast into a slab, the slab was heated at 1100 ° C for 1 hour, and then hot rolled to a thickness of 2.3 mm Went. The finishing temperature of hot rolling was 800 ° C. and the winding temperature was 610 ° C. After winding, pickling was performed, and hot rolled sheet annealing was performed at 1000 ° C. × 30 s. Thereafter, cold rolling to a sheet thickness of 0.35 mm, finish annealing for 30 seconds at the finish annealing temperature shown in Table 4, and further carburizing under the carburizing conditions shown in Table 4 to obtain steel plates No. 18-24 Produced. Then, measurement of Vickers hardness (load 10 g) and C amount in the plate thickness direction, and magnetic characteristics (W 10/400 , B50) and fatigue limit were performed by the above methods.
結果を表4に示す。成分および鋼板表層部の硬度を本発明の範囲内に制御した発明例である鋼板No.20〜23では、B50が1.60T以上、W10/400が23W/kg以下で、330MPa以上の疲労限が得られることがわかる。 The results are shown in Table 4. In steel plate Nos. 20 to 23, which are invention examples in which the hardness of the component and the steel sheet surface layer is controlled within the scope of the present invention, B50 is 1.60 T or more, W 10/400 is 23 W / kg or less, and a fatigue limit of 330 MPa or more It can be seen that
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