JPH0949065A - Wear resistant hot rolled steel sheet excellent in stretch-flanging property and its production - Google Patents
Wear resistant hot rolled steel sheet excellent in stretch-flanging property and its productionInfo
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- JPH0949065A JPH0949065A JP20089695A JP20089695A JPH0949065A JP H0949065 A JPH0949065 A JP H0949065A JP 20089695 A JP20089695 A JP 20089695A JP 20089695 A JP20089695 A JP 20089695A JP H0949065 A JPH0949065 A JP H0949065A
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Abstract
Description
【０００１】[0001]
【発明の属する技術分野】本発明は、伸びフランジ性を
はじめとする加工性にすぐれ、しかも、成形加工後の焼
き入れ処理等によってすぐれた耐摩耗性を付与し得る耐
摩耗用熱延鋼板とその製造方法に関する。TECHNICAL FIELD The present invention relates to a hot-rolled steel sheet for wear, which has excellent workability such as stretch-flangeability and can impart excellent wear resistance by quenching treatment after forming. The manufacturing method is related.
【０００２】[0002]
【従来の技術】自動車のオートマチック・トランスミッ
ション部品やそのトルクコンバータ部品等を含む種々の
駆動伝達部品は、従来、プレス成形後に、表面硬化によ
って耐摩耗性を付与するために、浸炭窒化処理、ガス軟
窒化処理、塩浴窒化処理等をしたり、或いは焼き入れ焼
戻し処理を行ない、更に、熱処理歪み取りを行なって、
高強度材とする方法にて製造されている。2. Description of the Related Art Various drive transmission components including automobile automatic transmission components and their torque converter components have conventionally been subjected to carbonitriding and gas softening treatment in order to impart wear resistance by surface hardening after press molding. Nitriding treatment, salt bath nitriding treatment, etc., or quenching and tempering treatment, and further heat treatment strain relief,
It is manufactured by the method of making a high strength material.
【０００３】しかし、これらの種々の熱処理は、プレス
成形後の部品の全表面を硬化させるので、その後の工程
として、溶接を必要とする場合には、その部位の硬化部
を切削によって削除する方法等が採られており、製造工
程数が多く、製造費用を高くしている。また、熱処理に
よって発生する形状変形をプレス等で手直しを行なう場
合、そのための切削工程も、製造費用を高めることとな
る。However, since these various heat treatments harden the entire surface of the part after press molding, when welding is required as a subsequent step, the hardened part of the part is removed by cutting. Etc. are adopted, the number of manufacturing steps is large, and the manufacturing cost is high. Further, when the shape deformation caused by the heat treatment is reworked by a press or the like, the cutting process therefor also increases the manufacturing cost.
【０００４】そこで、近年、自動車の軽量化や製造費用
の低減を図るために、上述したような自動車用の種々の
駆動伝達部品の製造方法の見直しがなされた結果、必要
な部位のみを表面硬化させて、耐摩耗性を付与する急速
加熱焼き入れ法が検討されている。Therefore, in recent years, in order to reduce the weight of automobiles and reduce the manufacturing cost, the manufacturing method of various drive transmission components for automobiles as described above has been reviewed, and as a result, only the necessary portions are surface-hardened. Therefore, a rapid heating and quenching method for imparting wear resistance has been studied.
【０００５】しかし、従来の鋼板では、加工性を考慮し
て、炭素の添加量が極力低く抑えられているので、この
ような鋼板については、これに急速加熱焼入れを行なっ
ても、必要とする表面硬さを得ることができない。この
ような従来の鋼板に急速加熱焼入れによって所要の部位
のみを硬化させるには、鋼板における炭素の量をはじめ
とする化学成分量を高めて、焼入れ性を向上させること
が必要となる。しかし、このように、焼入れ性を向上さ
せるために、炭素やその他の合金成分の添加量を高めれ
ば、反面、鋼板の加工性、特に、バーリング加工におい
て、穴緑部から割れが発生して、加工できないという欠
点がある。However, in conventional steel sheets, the amount of carbon added is kept as low as possible in consideration of the workability, and therefore such steel sheets are required even if they are subjected to rapid heating and quenching. The surface hardness cannot be obtained. In order to harden only a required portion of such a conventional steel sheet by rapid heating and quenching, it is necessary to increase the amount of chemical components such as the amount of carbon in the steel sheet and improve the hardenability. However, in this way, in order to improve the hardenability, if the addition amount of carbon and other alloy components is increased, on the other hand, the workability of the steel sheet, in particular, in the burring process, cracks occur from the green part of the hole, It has the drawback that it cannot be processed.
【０００６】[0006]
【発明が解決しようとする課題】本発明は、自動車用駆
動伝達部品の製造における従来の方法における上述した
ような問題を解決するためになされたものであって、鋼
の化学成分を適切に選択すると共に、その製造条件を適
切に選択することによって、すぐれた加工性を保持しな
がら耐摩耗性を付与し得る熱間圧延鋼板と、そのような
熱間圧延鋼板の製造方法を提供することを目的とする。SUMMARY OF THE INVENTION The present invention has been made to solve the above-mentioned problems in the conventional method for manufacturing drive transmission components for automobiles, and appropriately selects the chemical composition of steel. In addition, by appropriately selecting the production conditions, it is possible to provide a hot-rolled steel sheet capable of imparting wear resistance while maintaining excellent workability, and a method for producing such a hot-rolled steel sheet. To aim.
【０００７】[0007]
【課題を解決するための手段】本発明による伸びフラン
ジ性にすぐれる耐摩耗用熱延鋼板は、重量％にてＣ
0.２０〜0.３３％、Ｓｉ 0.０１〜0.５％、Ｍｎ 0.１
５〜0.８％、Ｐ 0.０３％以下、Ｓ 0.０２％以
下、sol.Ａｌ 0.０８％以下、Ｃｒ 0.１５〜0.７％、
Ｎ 0.０１％以下、を含み、残部鉄及び不可避的不純
物よりなり、パーライトを含んでいてよいフェライト・
ベイナイト混合組織を有することを特徴とする。The hot-rolled steel sheet for wear resistance having excellent stretch flangeability according to the present invention is C in weight%.
0.20-0.33%, Si 0.01-0.5%, Mn 0.1
5 to 0.8%, P 0.03% or less, S 0.02% or less, sol.Al 0.08% or less, Cr 0.15 to 0.7%,
Ferrite containing N 0.01% or less, the balance iron and unavoidable impurities, and may contain pearlite.
It is characterized by having a bainite mixed structure.
【０００８】このようなパーライトを含んでいてよいフ
ェライト・ベイナイト混合組織を有して、伸びフランジ
性にすぐれる耐摩耗用熱延鋼板は、本発明に従って、上
記化学成分を有する鋼をＡr3点以上の仕上温度で熱間圧
延し、その後、巻取温度まで、平均冷却速度２０〜８０
℃／秒にて冷却した後、４００〜６００℃の範囲の温度
で巻取ることによって得ることができる。A wear-resistant hot-rolled steel sheet having a ferrite / bainite mixed structure which may contain such pearlite and having excellent stretch flangeability is obtained according to the present invention by using a steel having the above chemical composition as Ar 3 point. Hot rolling is performed at the above finishing temperature, and thereafter, the average cooling rate is 20 to 80 until the coiling temperature.
It can be obtained by cooling at a rate of 400C / sec and then winding at a temperature in the range of 400 to 600C.
【０００９】[0009]
【発明の実施の形態】先ず、本発明による鋼の化学成分
の限定理由について説明する。Ｃは、鋼板の強度を高め
るために有効な元素であり、また、低温変態生成物であ
るベイナイトを生成させるための必須元素であり、更
に、焼入れ性を高める作用を有する。本発明において
は、このような効果を有効に得るために、特に、急速加
熱焼入れによって、所要の表面硬さを確保するために
も、添加量は少なくとも0.２０％が必要である。しか
し、添加量が過多になれば、延性と伸びフランジ性、更
に、溶接性も劣化するので、添加量の上限は0.３３％と
する。BEST MODE FOR CARRYING OUT THE INVENTION First, the reasons for limiting the chemical composition of steel according to the present invention will be explained. C is an element effective for increasing the strength of the steel sheet, is an essential element for forming bainite which is a low temperature transformation product, and further has an effect of enhancing hardenability. In the present invention, in order to effectively obtain such effects, in particular, in order to secure a required surface hardness by rapid heating and quenching, the addition amount is required to be at least 0.20%. However, if the added amount is too large, the ductility, stretch flangeability, and weldability deteriorate, so the upper limit of the added amount is 0.33%.
【００１０】Ｓｉは、本発明における混合組織を得るた
めに必要であり、また、強度と延性を高めるのに有用な
元素であり、更に、溶鋼の脱酸や焼入れ性にも、有用な
元素である。このような効果を有効に得るためには、少
なくとも0.０１％の添加が必要であるが、しかし、過多
に添加するときは、熱間圧延時にＳｉスケールが発生し
やすくなり、鋼板の表面性状が劣化するので、上限を0.
５％とする。Si is an element necessary for obtaining the mixed structure in the present invention, and is a useful element for enhancing the strength and ductility, and is also a useful element for deoxidizing and quenching the molten steel. is there. In order to effectively obtain such an effect, it is necessary to add at least 0.01%. However, when it is added excessively, Si scale is likely to occur during hot rolling, and the surface properties of the steel sheet are Is deteriorated, the upper limit is 0.
5%.
【００１１】Ｍｎは、焼入れ性を向上させ、強度を高め
る元素であると共に、未変態のオーステナイトをベイナ
イトに変態させるのにも必要である。これらの効果を有
効に得るためには、少なくとも0.１５％の添加を必要と
する。しかし、0.８％を超えるときは、強度が高くなる
ので、添加量の上限を0.７％とする。Ｐは、これを0.０
３％を超えて多量に添加するときは、絞り加工後の遷移
温度を上昇させるので、0.０３％以下の範囲とする。Mn is an element that improves hardenability and strength, and is also necessary for transforming untransformed austenite into bainite. To obtain these effects effectively, addition of at least 0.15% is required. However, if it exceeds 0.8%, the strength becomes high, so the upper limit of the addition amount is made 0.7%. P does this
When a large amount is added in excess of 3%, the transition temperature after drawing is increased, so the content is made 0.03% or less.
【００１２】Ｓは、これを0.０２％を超えて多量に添加
させるときは、伸びフランジ性を劣化させるので、0.０
２％以下とする。sol.Ａｌは、鋼の脱酸剤として添加さ
れるが、しかし、過多に添加するときは、鋼の清浄度が
悪くなり、靱性が低下するので、0.８％以下とする。When S is added in a large amount exceeding 0.02%, S deteriorates the stretch flangeability, so 0.0% is added.
2% or less. Although sol.Al is added as a deoxidizing agent for steel, however, if excessively added, the cleanliness of the steel deteriorates and the toughness decreases, so the content is made 0.8% or less.
【００１３】Ｃｒは、鋼の強度及び焼入れ性を高める元
素であり、この観点からは、少なくとも0.１５％を添加
することが必要であるが、しかし、過多に添加するとき
は、溶接性を悪くするので、上限を0.７％とする。Ｎ
は、多量に含有させるときは、加工性が劣化すると共
に、ＢＮを形成して、焼入れ性を劣化させるので、0.０
１％以下とする。[0013] Cr is an element that enhances the strength and hardenability of steel. From this viewpoint, it is necessary to add at least 0.15%. However, when it is added excessively, weldability is increased. As it will worsen, the upper limit is 0.7%. N
When it is contained in a large amount, the workability deteriorates, and BN is formed to deteriorate the hardenability.
1% or less.
【００１４】本発明においては、上記した元素に加え
て、鋼にＣｕ 0.５％以下、Ｎｉ 0.３％以下、Ｍｏ
0.０５〜0.３０％、Ｃａ 0.０００５〜0.０１％よりな
る群から選ばれる少なくとも１種の元素を添加すること
ができる。In the present invention, in addition to the above-mentioned elements, in the steel, Cu 0.5% or less, Ni 0.3% or less, Mo
At least one element selected from the group consisting of 0.05 to 0.30% and Ca 0.0005 to 0.01% can be added.
【００１５】Ｎｉは、強度や靱性、更には、焼入れ性を
向上させる効果を有しているので、鋼板により高度の靱
性や焼入れ性を要求される場合に、必要に応じて、添加
される。しかし、添加量が0.５％以上では、その効果が
飽和するので、鋼製造の経済性を考慮して、添加量は、
0.３％以下の範囲とする。Ｍｏは、焼入れ性を向上さ
せ、また、焼入れ後の靱性を向上させる元素であって、
これらの効果を有効に得るためには、少なくとも0.０５
％の添加を必要とする。しかし、添加量が0.３％を超え
るときは、強度が高くなるので、添加量の上限は0.３０
％とする。Ni has the effect of improving strength and toughness as well as hardenability, so Ni is added as necessary when a steel sheet is required to have high toughness and hardenability. However, if the addition amount is 0.5% or more, the effect will be saturated, so in consideration of the economical efficiency of steel production, the addition amount is
The range is 0.3% or less. Mo is an element that improves hardenability and also improves toughness after quenching.
To obtain these effects effectively, at least 0.05
% Addition is required. However, when the amount added exceeds 0.3%, the strength increases, so the upper limit of the amount added is 0.30.
%.
【００１６】Ｃｕは、Ｎｉとほぼ同様の効果を有し、よ
り一層の強度や焼入れ性が要求され場合に、必要に応じ
て、添加される。しかし、過剰の添加は、熱間加工にお
いてＣｕヘゲが発生し、製造困難となるため、添加量は
0.５％以下とする。Ｃａは、硫化物を展伸状から球状に
する形態制御を通じて、鋼板の機械的異方性を小さく
し、延性と靱性を改善する効果がある。この効果を有効
に得るためには、少なくとも0.０００５％以上の添加が
必要であるが、しかし、0.０１％を超えるときは、鋼中
の非金属介在物が増大して、延性や靱性が低下する。Cu has an effect similar to that of Ni, and is added as needed when higher strength and hardenability are required. However, excessive addition causes Cu hegging during hot working, which makes manufacturing difficult.
0.5% or less. Ca has the effect of reducing the mechanical anisotropy of the steel sheet and improving the ductility and toughness by controlling the morphology of the sulfide from a stretched shape to a spherical shape. In order to obtain this effect effectively, it is necessary to add at least 0.0005% or more. However, when it exceeds 0.01%, the nonmetallic inclusions in the steel increase and the ductility and toughness increase. Is reduced.
【００１７】本発明による熱延鋼板は、このように、パ
ーライトを含んでいてよいフェライト・ベイナイト混合
組織を有する。このようなフェライト中に生成するベイ
ナイトは、鋼板の強度を確保しつつ、強度と共に伸びフ
ランジ性をバランスよく向上させるのに有用な組織であ
る。これに対して、マルテンサイト組織やパーライト組
織が生じた場合には、高強度化し、これに伴って伸びフ
ランジ性を劣化させる。The hot-rolled steel sheet according to the present invention thus has a ferrite-bainite mixed structure which may contain pearlite. The bainite formed in such a ferrite is a structure that is useful for improving the strength and stretch flangeability in a well-balanced manner while ensuring the strength of the steel sheet. On the other hand, when a martensite structure or a pearlite structure is generated, the strength is increased and the stretch flangeability is deteriorated accordingly.
【００１８】従って、本発明による熱延鋼板は、フェラ
イト・ベイナイト混合組織を主体とし、パーライトを含
んでいてもよく、このパーライトには、擬似パーライト
を含むものとするが、しかし、好ましくは、パーライト
を含まず、フェライト・ベイナイト混合組織からなるも
のである。Therefore, the hot-rolled steel sheet according to the present invention may be mainly composed of a ferrite / bainite mixed structure and may contain pearlite. The pearlite contains pseudo pearlite, but preferably contains pearlite. Instead, it has a mixed structure of ferrite and bainite.
【００１９】本発明によれば、このような熱延鋼板は、
前述したような所定の化学成分を有する鋼をＡr3点以上
の仕上温度で熱間圧延し、その後、巻取温度まで、平均
冷却速度２０〜８０℃／秒にて冷却した後、４００〜６
００℃の範囲の温度で巻取ることによって得ることがで
きる。According to the present invention, such a hot rolled steel sheet is
Steel having a predetermined chemical composition as described above is hot-rolled at a finishing temperature of 3 or more points of Ar and then cooled to a coiling temperature at an average cooling rate of 20 to 80 ° C./sec.
It can be obtained by winding at a temperature in the range of 00 ° C.
【００２０】熱間圧延において、仕上温度はオーステナ
イト域、即ち、Ａr3点以上の温度域である。仕上温度が
Ａr3点よりも低いときは、２相域圧延となり、フェライ
ト粒の加工組織が残存して、得られる熱延鋼板の特性を
極端に劣化させる。In hot rolling, the finishing temperature is in the austenite range, that is, the temperature range of Ar 3 points or higher. When the finishing temperature is lower than the Ar 3 point, the rolling occurs in the two-phase region, and the worked structure of the ferrite grains remains, and the properties of the obtained hot-rolled steel sheet are extremely deteriorated.
【００２１】本発明によれば、このような熱間圧延の
後、巻取温度まで、平均冷却速度２０〜８０℃／秒にて
冷却した後、４００〜６００℃の範囲の温度で巻取る。
巻取温度が４００℃よりも低いか、又は巻取までの平均
冷却速度が８０℃／秒を超えるときは、ミクロ組織中に
マルテンサイトが生成し、強度が高くなり、延性が劣化
する。他方、巻取温度が６００℃よりも高いか、又は巻
取までの平均冷却速度が２０℃／秒未満のときは、ミク
ロ組織中にベイナイトが生成せず、代わりにパーライト
が生成して、伸びフランジ性が低下する。即ち、目的す
るフェライト・ベイナイト混合組織を主体とする熱延鋼
板を得ることができない。According to the present invention, after such hot rolling, it is cooled to the coiling temperature at an average cooling rate of 20 to 80 ° C./sec and then coiled at a temperature in the range of 400 to 600 ° C.
When the coiling temperature is lower than 400 ° C. or when the average cooling rate until coiling exceeds 80 ° C./sec, martensite is generated in the microstructure, the strength becomes high, and the ductility deteriorates. On the other hand, when the coiling temperature is higher than 600 ° C. or the average cooling rate until coiling is less than 20 ° C./sec, bainite is not formed in the microstructure, and pearlite is formed instead, which causes elongation. Flangeability deteriorates. That is, it is not possible to obtain a desired hot-rolled steel sheet mainly composed of a ferrite-bainite mixed structure.
【００２２】このような本発明による熱延鋼板は、伸び
フランジ性がすぐれており、高加工を伴うプレス成形の
用途に好適に用いることができ、しかも、高周波、電子
ビーム、レザー等の急速加熱焼入れによって、所要の部
位に所要の表面硬さを与えて、耐摩耗性とすることがで
きる。Such a hot-rolled steel sheet according to the present invention has excellent stretch-flangeability and can be suitably used for press-forming applications involving high working, and furthermore, rapid heating of high frequency, electron beam, laser, etc. By quenching, it is possible to impart a required surface hardness to a required portion and make it wear resistant.
【００２３】[0023]
【実施例】表１に示す化学成分を有する供試鋼を溶製
し、表２に示す熱延条件で熱間圧延し、巻取って、熱延
鋼板を製造した。表１中、供試鋼番号１〜３及び６〜９
は本発明鋼であり、他の供試鋼番号４、５、１０及び１
１は比較鋼である。得られた熱延鋼板について、引張特
性及び穴拡げ率（λ）を求め、更に、ミクロ組織を調べ
た。ここに、穴拡げ率（λ）とは、直径６０mmの鋼板の
中央部に直径１０mmの穴を打抜き、これを押し拡げて、
板厚方向にクラックが貫通するまで、穴拡げを行なっ
て、最初の打抜き穴の直径をｄ0 （mm）とし、クラック
が発生したときの穴の直径をｄ（mm）とするとき、λ＝
〔（ｄ−ｄ0 ）／ｄ0 〕×１００（％）で表わされる。Example A sample steel having the chemical composition shown in Table 1 was melted, hot-rolled under the hot-rolling conditions shown in Table 2, and wound to produce a hot-rolled steel sheet. In Table 1, sample steel Nos. 1 to 3 and 6 to 9
Is a steel of the present invention, and other steels under test Nos. 4, 5, 10 and 1
1 is a comparative steel. The tensile properties and the hole expansion ratio (λ) of the obtained hot-rolled steel sheet were determined, and the microstructure was further examined. Here, the hole expansion rate (λ) means that a hole with a diameter of 10 mm is punched out in the center of a steel plate with a diameter of 60 mm, and this is pushed and expanded.
When the diameter of the first punched hole is d 0 (mm) and the diameter of the hole when the crack is generated is d (mm), λ =
It is represented by [(d−d 0 ) / d 0 ] × 100 (%).
【００２４】また、得られた熱延鋼板について、カップ
状の絞り成形を行ない、成形品を１５０ＫＨｚで９２５
〜９８０℃の表面温度に加熱し、５秒間保持した後、水
冷する高周波焼入れを施し、その表面硬さ（ＨＲＣ）を
測定した。その結果を表２及び表３に示す。表２及び表
３において、試験番号５、６、１３及び１４は、用いた
鋼の化学成分が本発明で規定する範囲外にあり、試験番
号１５〜１８は、熱間圧延の条件が本発明で規定する範
囲外にある。The hot-rolled steel sheet thus obtained was subjected to cup-shaped drawing, and the molded product was subjected to 925 at 150 KHz.
After heating to a surface temperature of ˜980 ° C. and holding for 5 seconds, induction hardening was performed by cooling with water, and the surface hardness (HRC) was measured. The results are shown in Tables 2 and 3. In Tables 2 and 3, Test Nos. 5, 6, 13 and 14 have the chemical composition of the steel used outside the range specified in the present invention, and Test Nos. 15 to 18 have hot rolling conditions of the present invention. It is outside the range specified in.
【００２５】表２に示す結果から、本発明の熱延条件で
得られた本発明鋼（試験番号１〜４及び７〜１２）は、
その組織がベイナイト・フエライト混合組織であり、λ
は７４％以上、延性は２９％以上であって、すぐれた特
性を有する。これに対して、比較鋼（試験番号５及び１
４）では、熱延条件が本発明で規定する範囲内にあって
も、λは６０％以下の低いレベルにとどまっている。ま
た、高周波焼入れによる表面硬さは、本発明鋼では十分
な硬さを得ることができる。しかし、比較鋼（試験番号
６及び１３においては、λ値は比較的高いが、表面硬さ
が低いので、耐摩耗性が劣る。From the results shown in Table 2, the steels of the present invention (test numbers 1 to 4 and 7 to 12) obtained under the hot rolling conditions of the present invention are:
Its structure is a bainite-ferrite mixed structure, and λ
Has an excellent property of 74% or more and a ductility of 29% or more. In contrast, comparative steels (test numbers 5 and 1
In 4), λ remains at a low level of 60% or less even when the hot rolling conditions are within the range specified by the present invention. As for the surface hardness by induction hardening, the steel of the present invention can obtain a sufficient hardness. However, in Comparative Steels (Test Nos. 6 and 13, the λ value is relatively high, but the surface hardness is low, so the wear resistance is poor.
【００２６】また、第３表に示すように、熱間圧延後の
冷却速度が本発明で規定する下限より遅いときは、試験
番号１５から理解されるように、その組織がフェライト
・パーライト組織であるために、λが４５％と低い。他
方、熱間圧延後の冷却速度が本発明で規定する上限より
早いときは、試験番号１６にみられるように、組織がフ
ェライト・ベイナイト・マルテンサイト組織であり、強
度が高すぎて、延性が低く、加工性に劣る。巻取温度が
本発明で規定する下限よりも低いときは、試験番号１７
から明らなように、延性が劣る。しかし、試験番号１８
にみられるように、巻取温度が本発明で規定する上限よ
りも高いときは、フェライト・パーライト組織となり、
λ値が低い。Further, as shown in Table 3, when the cooling rate after hot rolling is lower than the lower limit specified in the present invention, as understood from Test No. 15, the structure is a ferrite-pearlite structure. Therefore, λ is as low as 45%. On the other hand, when the cooling rate after hot rolling is faster than the upper limit specified in the present invention, the structure is a ferrite-bainite-martensite structure as seen in Test No. 16, the strength is too high, and the ductility is low. Low and inferior in workability. When the winding temperature is lower than the lower limit specified in the present invention, test number 17
As is clear from the above, ductility is poor. However, test number 18
As can be seen from the above, when the winding temperature is higher than the upper limit specified in the present invention, a ferrite-pearlite structure is formed,
Low λ value.
【００２７】[0027]
【表１】 [Table 1]
【００２８】[0028]
【表２】 [Table 2]
【００２９】[0029]
【表３】 [Table 3]
Claims (4)
物よりなり、パーライトを含んでいてよいフェライト・
ベイナイト混合組織を有することを特徴とする伸びフラ
ンジ性にすぐれる耐摩耗用熱延鋼板。1. In weight%, C 0.20 to 0.33%, Si 0.01 to 0.5%, Mn 0.15 to 0.8%, P 0.03% or less, S 0.02. % Or less, sol.Al 0.08% or less, Cr 0.15 to 0.7%, N 0.01% or less, the balance consisting of iron and unavoidable impurities, and may include pearlite.
A wear-resistant hot-rolled steel sheet excellent in stretch-flangeability, characterized by having a bainite mixed structure.
下、 Ｎｉ 0.３％以下、 Ｍｏ 0.０５〜0.３０％、 Ｃａ 0.０００５〜0.０１％よりなる群から選ばれる少
なくとも１種の元素を含み、残部鉄及び不可避的不純物
よりなり、パーライトを含んでいてよいフェライト・ベ
イナイト混合組織を有することを特徴とする伸びフラン
ジ性にすぐれる耐摩耗用熱延鋼板。2. In% by weight, (a) C 0.20 to 0.33%, Si 0.01 to 0.5%, Mn 0.15 to 0.8%, P 0.03% or less, S 0.02% or less, sol.Al 0.08% or less, Cr 0.15 to 0.7%, N 0.01% or less, and (b) Cu 0.5% or less, Ni 0.3. % Or less, Mo 0.05 to 0.30%, Ca 0.0005 to 0.01%, and at least one element selected from the group consisting of iron and inevitable impurities, and pearlite. A wear-resistant hot-rolled steel sheet having excellent stretch-flange formability, which has a good mixed structure of ferrite and bainite.
物よりなる鋼をＡr3点以上の仕上温度で熱間圧延し、そ
の後、巻取温度まで、平均冷却速度２０〜８０℃／秒に
て冷却した後、４００〜６００℃の範囲の温度で巻取る
ことを特徴とするパーライトを含んでいてよいフェライ
ト・ベイナイト混合組織を有する伸びフランジ性にすぐ
れる耐摩耗用熱延鋼板。3. In% by weight, C 0.20 to 0.33%, Si 0.01 to 0.5%, Mn 0.15 to 0.8%, P 0.03% or less, S 0.02. % Or less, sol.Al 0.08% or less, Cr 0.15 to 0.7%, N 0.01% or less, and the balance iron and unavoidable impurities at a finishing temperature of 3 or more Ar. Ferrites that may contain pearlite, characterized by being hot-rolled, then cooled to the coiling temperature at an average cooling rate of 20-80 ° C / sec and then coiled at a temperature in the range of 400-600 ° C. -Abrasion resistant hot rolled steel sheet having a bainite mixed structure and excellent stretch flangeability.
下、 Ｎｉ 0.３％以下、 Ｍｏ 0.０５〜0.３０％、 Ｃａ 0.０００５〜0.０１％よりなる群から選ばれる少
なくとも１種の元素を含み、残部鉄及び不可避的不純物
よりなる鋼をＡr3点以上の仕上温度で熱間圧延し、その
後、巻取温度まで、平均冷却速度２０〜８０℃／秒にて
冷却した後、４００〜６００℃の範囲の温度で巻取るこ
とを特徴とするパーライトを含んでいてよいフェライト
・ベイナイト混合組織を有する伸びフランジ性にすぐれ
る耐摩耗用熱延鋼板。4. In% by weight, (a) C 0.20 to 0.33%, Si 0.01 to 0.5%, Mn 0.15 to 0.8%, P 0.03% or less, S 0.02% or less, sol.Al 0.08% or less, Cr 0.15 to 0.7%, N 0.01% or less, and (b) Cu 0.5% or less, Ni 0.3. % or less, Mo 0.05 to 0.30%, comprising at least one element selected from the group consisting of Ca 0.0005 to 0.01%, the steel consisting of the balance of iron and unavoidable impurities than the Ar 3 point The pearlite is characterized in that it is hot-rolled at a finishing temperature of, then cooled to a coiling temperature at an average cooling rate of 20 to 80 ° C./sec, and then coiled at a temperature in the range of 400 to 600 ° C. A wear-resistant hot-rolled steel sheet having a good ferrite-bainite mixed structure and having excellent stretch-flange formability.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP20089695A JPH0949065A (en) | 1995-08-07 | 1995-08-07 | Wear resistant hot rolled steel sheet excellent in stretch-flanging property and its production |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP20089695A JPH0949065A (en) | 1995-08-07 | 1995-08-07 | Wear resistant hot rolled steel sheet excellent in stretch-flanging property and its production |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH0949065A true JPH0949065A (en) | 1997-02-18 |
Family
ID=16432062
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP20089695A Pending JPH0949065A (en) | 1995-08-07 | 1995-08-07 | Wear resistant hot rolled steel sheet excellent in stretch-flanging property and its production |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0949065A (en) |
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-
1995
- 1995-08-07 JP JP20089695A patent/JPH0949065A/en active Pending
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| WO2007116599A1 (en) | 2006-03-31 | 2007-10-18 | Jfe Steel Corporation | Steel plate having excellent fine blanking processability and method for manufacture thereof |
| AU2010215076B2 (en) * | 2009-02-20 | 2016-02-04 | Nucor Corporation | A hot rolled thin cast strip product and method for making the same |
| WO2010094075A1 (en) * | 2009-02-20 | 2010-08-26 | Bluescope Steel Limited | A hot rolled thin cast strip product and method for making the same |
| US8444780B2 (en) | 2009-02-20 | 2013-05-21 | Nucor Corporation | Hot rolled thin cast strip product and method for making the same |
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| WO2010123315A3 (en) * | 2009-04-23 | 2011-03-10 | 주식회사 포스코 | High strength, high toughness steel wire rod, and method for manufacturing same |
| WO2012141297A1 (en) * | 2011-04-13 | 2012-10-18 | 新日本製鐵株式会社 | Hot-rolled steel for gaseous nitrocarburizing and manufacturing method thereof |
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| CN103534379B (en) * | 2011-04-13 | 2016-01-20 | 新日铁住金株式会社 | Gas nitrocarburizing hot-rolled steel sheet and manufacture method thereof |
| CN103534379A (en) * | 2011-04-13 | 2014-01-22 | 新日铁住金株式会社 | Hot-rolled steel for gaseous nitrocarburizing and manufacturing method thereof |
| CN103459648A (en) * | 2011-04-13 | 2013-12-18 | 新日铁住金株式会社 | Hot-rolled steel sheet and manufacturing method thereof |
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