JP2002020837A - Wear resistant steel excellent in toughness and its production method - Google Patents
Wear resistant steel excellent in toughness and its production methodInfo
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- JP2002020837A JP2002020837A JP2000205313A JP2000205313A JP2002020837A JP 2002020837 A JP2002020837 A JP 2002020837A JP 2000205313 A JP2000205313 A JP 2000205313A JP 2000205313 A JP2000205313 A JP 2000205313A JP 2002020837 A JP2002020837 A JP 2002020837A
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- steel
- toughness
- austenite grain
- less
- wear
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Abstract
Description
【０００１】[0001]
【発明の属する技術分野】本発明は、建設,土木および
鉱山等での堀削作業で用いられる産業機械、運搬機器等
に用いられる靭性に優れた耐摩耗鋼およびその製造方法
に関する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to an abrasion-resistant steel having excellent toughness used for industrial machines, transportation equipment and the like used for excavation work in construction, civil engineering and mining, and a method for producing the same.
【０００２】[0002]
【従来の技術】建設、土木および鉱山等での堀削作業で
用いられる産業機械、運搬機器（例えば、パワーショベ
ル、ブルドーザ、大型ダンプトラック等）の土砂摩耗部
は、その摩耗量によって寿命がきまるため、耐摩耗性に
優れた鋼材が要求され、鋼材の硬度を高め、耐摩耗性を
向上させることが行われている。2. Description of the Related Art The life of an earth and sand portion of an industrial machine or a transporting device (eg, a power shovel, a bulldozer, a large dump truck, etc.) used in construction, excavation work in civil engineering and mining, etc. is determined by the amount of wear. Therefore, a steel material having excellent wear resistance is required, and it has been performed to increase the hardness of the steel material and improve the wear resistance.
【０００３】鋼材の硬度はマルテンサイト組織の場合、
鋼中Ｃ量によって一義的に決定され、硬度を高めるため
には多量のＣ添加を必要とするものの、靭性が著しく劣
化するという問題があった。[0003] In the case of martensite structure, the hardness of steel
It is uniquely determined by the amount of C in steel, and although a large amount of C is required to increase hardness, there is a problem that toughness is significantly deteriorated.
【０００４】そのため、焼入れ性と靭性の両者を確保す
る成分組成が検討され、更に、圧延した鋼材を空冷後に
再加熱し、旧オーステナイト粒を微細化すること、再加
熱時の旧オーステナイト粒の粗大化を析出物等で抑制す
る技術が提案されてきた。[0004] Therefore, the composition of components for ensuring both hardenability and toughness has been studied. Further, the rolled steel material is reheated after air cooling to refine the old austenite grains, and the coarseness of the old austenite grains upon reheating. Techniques for suppressing the formation by precipitation or the like have been proposed.
【０００５】特開平１０−１０２１８５号公報には、オ
ーステナイト再結晶域で圧延を行い、旧オーステナイト
粒を微細化させ、その後、再加熱時にＣｒ，Ｍｏ，Ｖを
固溶させ、焼入れ、焼戻しすれば、時間経過後、それら
の複合析出物が形成され耐摩耗性が向上し、靭性に有害
なＣ，Ｍｎ等を削減できることが記載されている。[0005] Japanese Patent Application Laid-Open No. 10-102185 discloses that rolling is performed in an austenite recrystallization region to refine old austenite grains, and then Cr, Mo, and V are solid-dissolved during reheating, quenched, and tempered. It describes that after a lapse of time, these composite precipitates are formed, the wear resistance is improved, and C and Mn, which are harmful to toughness, can be reduced.
【０００６】特開平１１−７１６３１号公報には、Ｃ量
を低下し、焼入れ性の低下はＳｉにより補償し、さらに
Ｎｂのピンニング効果により再加熱時のオーステナイト
粒の粗大化を防止し、靭性を高める技術が開示されてい
る。Japanese Patent Application Laid-Open No. 11-71631 discloses that the C content is reduced, the hardenability is compensated by Si, and the austenite grains are prevented from becoming coarse during reheating by the pinning effect of Nb, and the toughness is reduced. Techniques for enhancing are disclosed.
【０００７】しかし、これらの従来技術は再加熱焼入れ
プロセスによるもので、直接焼入れと比較して製造コス
トが上昇し、また、合金元素としてＣｒ，Ｍｏ，Ｖ，Ｎ
ｂの添加が必要であった。However, these prior arts are based on a reheating quenching process, which increases the production cost as compared with direct quenching, and also includes Cr, Mo, V, and N as alloying elements.
The addition of b was required.
【０００８】直接焼入れの場合、再加熱焼入れと比較し
て、再加熱処理がなく旧オーステナイト粒が粗大化し、
靭性が劣化するため、旧オーステナイト粒の微細化がポ
イントとなる。[0008] In the case of direct quenching, compared with reheating quenching, there is no reheating treatment, and old austenite grains are coarsened.
Since toughness is deteriorated, the key point is to refine the prior austenite grains.
【０００９】特開平８−４１５３５号公報は、ＳｉとＮ
ｂを複合添加した鋼を直接焼入れ、焼戻すことで焼戻し
脆化と焼戻し軟化を同時に抑制し、Ｎｂによる旧オース
テナイト粒微細化で、耐摩耗性（ＨＢ５００以上）と靭
性を両立させ、Ｍｏを添加して焼入れ性および靭性を更
に向上させる技術を開示している。Japanese Patent Application Laid-Open No. 8-41535 discloses that Si and N
By directly quenching and tempering the steel to which b is added in combination, tempering embrittlement and tempering softening are suppressed at the same time, and abrasion resistance (HB 500 or more) and toughness are compatible with the austenite grain refinement by Nb, and Mo is added. Discloses a technique for further improving the hardenability and toughness.
【００１０】[0010]
【発明が解決しようとする課題】しかしながら、上記技
術は、Ｓｉ量を増加させるため溶接部靭性が低下し、Ｎ
ｂ，Ｍｏ等高価な元素を添加した場合は、省プロセスに
よる製造コスト低下のメリットは失われる。また、得ら
れる鋼材の硬さは、ブリネル硬さ５００以上であり、建
設,土木および鉱山等での堀削作業で用いられる産業機
械、運搬機器等に用いられる耐摩耗鋼としては硬度が高
すぎ、靭性の向上が望めない。However, in the above-mentioned technique, the toughness of the welded portion is reduced because the Si content is increased, and the N content is reduced.
When expensive elements such as b and Mo are added, the advantage of lowering the manufacturing cost due to the saving of the process is lost. The hardness of the resulting steel material is Brinell hardness of 500 or more, which is too high for wear-resistant steel used in industrial machines, transportation equipment, and the like used in excavation work in construction, civil engineering, mining, and the like. , Improvement in toughness cannot be expected.
【００１１】本発明は、以上の点に鑑みなされたもの
で、高価な元素を添加せず、直接焼入れ焼戻しによりブ
リネル硬さ３００〜５００でｖＥ−４０℃：１７Ｊ以上
の靭性に優れた耐摩耗鋼およびその製造方法を提供する
ことを目的とする。The present invention has been made in view of the above points, and does not add expensive elements, and has a Brinell hardness of 300 to 500 and vE- 40 ° C : excellent toughness of 17 J or more by direct quenching and tempering. An object of the present invention is to provide steel and a method for manufacturing the same.
【００１２】[0012]
【課題を解決するための手段】本発明者らは、耐摩耗鋼
の靭性改善について鋭意検討を行い、ブリネル硬さ３０
０〜５００の場合、オーステナイト未再結晶域で強圧下
を行ない、オーステナイト粒を形態制御し、直接焼入
れ、焼戻しし、焼戻しマルテンサイト組織とした場合、
優れた靭性を有する耐摩耗鋼が得られることを見出し
た。Means for Solving the Problems The present inventors have made intensive studies on improving the toughness of wear-resistant steel and have found that the Brinell hardness is 30%.
In the case of 0 to 500, a strong reduction is performed in the austenite non-recrystallized region to control the form of the austenite grains, directly quenched, tempered, and a tempered martensite structure,
It has been found that a wear-resistant steel having excellent toughness can be obtained.
【００１３】本発明は以上の知見をもとに更に検討を加
えてなされたものである。The present invention has been made based on the above findings and further studied.
【００１４】１． 下記の組織を有することを特徴とす
る、質量％で、Ｃ：０．０５〜０．４０％、Ｓｉ：０．
１〜０．８％、Ｍｎ：０．５〜２．０％、Ｃｒ：０．１
〜２．０％、Ｔｉ：０．００５〜０．５％、Ｂ：０．０
００５〜０．００５％、Ａｌ：０．００５〜０．１０
％、Ｎ：０．００５％以下、残部実質的にＦｅおよび不
可避不純物とからなる耐摩耗鋼。1. C: 0.05 to 0.40% by mass, Si: 0.
1 to 0.8%, Mn: 0.5 to 2.0%, Cr: 0.1
To 2.0%, Ti: 0.005 to 0.5%, B: 0.0
005-0.005%, Al: 0.005-0.10
%, N: 0.005% or less, with the balance substantially consisting of Fe and unavoidable impurities.
【００１５】（１）旧オーステナイト粒展伸度（ｄＬ／
ｄＺ）：２以上の焼戻しマルテンサイト組織 但し、ｄＺ：鋼の肉厚方向の旧オーステナイト粒径、ｄ
Ｌ：鋼の圧延方向の旧オーステナイト粒径 ２． 鋼組成として更に、質量％で、Ｃｕ：０．１〜
１．０％、Ｎｉ：０．１〜１．０％、Ｍｏ：０．１〜
１．０％、Ｖ：０．０１〜０．２％の一種または二種以
上を含有する１記載の耐摩耗鋼。(1) Old austenite grain elongation (dL /
dZ): 2 or more tempered martensite structure, where dZ: prior austenite grain size in the thickness direction of steel, d
L: Old austenite grain size in the rolling direction of steel Further, as a steel composition, Cu: 0.1 to
1.0%, Ni: 0.1 to 1.0%, Mo: 0.1 to
1. The wear-resistant steel according to 1, which contains one or more of 1.0% and V: 0.01 to 0.2%.
【００１６】３． 鋼組成として更に、質量％で、Ｎ
ｂ：０．００５〜０．１％を含有する１または２記載の
耐摩耗鋼。3. Further, as a steel composition,
b: The wear-resistant steel according to 1 or 2 containing 0.005 to 0.1%.
【００１７】４． １乃至３の何れかに記載の組成を有
する鋼を、９００℃以下のオーステナイト未再結晶域に
おいて累積圧下率５０％以上で熱間圧延後、直ちにＡｒ
3点以上から焼入れし、その後３００℃〜Ａｃ1で焼戻し
することを特徴とする耐摩耗鋼の製造方法。4. Immediately after hot rolling a steel having the composition described in any one of 1 to 3 at a cumulative rolling reduction of 50% or more in an austenite unrecrystallized region of 900 ° C. or less, Ar
A method for producing wear-resistant steel, characterized by quenching from three or more points and then tempering at 300 ° C. to Ac1.
【００１８】[0018]
【発明の実施の形態】本発明の成分組成、ミクロ組織お
よび製造条件について説明する。BEST MODE FOR CARRYING OUT THE INVENTION The component composition, microstructure and production conditions of the present invention will be described.
【００１９】１．成分組成 Ｃ Ｃは、鋼材の硬度を高め、耐摩耗性を向上させるため添
加する。０．０５％未満ではその効果が得られず、一
方、０．４０％を超えると溶接性および靭性が低下し、
焼き割れおよび遅れ破壊が生じ易くなるため、０．０５
％以上、０．４０％以下（０．０５〜０．４０％）とす
る。好ましくは０．１０〜０．３５％とする。1. Component Composition C C is added to increase the hardness of the steel material and improve the wear resistance. If it is less than 0.05%, the effect cannot be obtained, while if it exceeds 0.40%, weldability and toughness decrease,
Since cracking and delayed fracture tend to occur, 0.05%
% To 0.40% or less (0.05 to 0.40%). Preferably, it is 0.10 to 0.35%.
【００２０】Ｓｉ Ｓｉは、製鋼時の脱酸剤として作用するため添加する。
０．１％未満ではその効果が十分でなく、一方、０．８
％を超えると溶接性、および靭性を損なうため、０．１
〜０．８％とする。好ましくは０．２５〜０．５５％と
する。Si Si is added because it acts as a deoxidizer during steelmaking.
If it is less than 0.1%, the effect is not sufficient.
%, The weldability and toughness are impaired.
To 0.8%. Preferably, it is 0.25 to 0.55%.
【００２１】Ｍｎ Ｍｎは、低コストで焼入れ性を高め,靭性を向上させる
ため添加する。０．５％未満ではその効果がなく、一
方、２．０％を超えると溶接性を損ない、また遅れ破壊
が生じ易くなるため、０．５〜２．０％とする。好まし
くは１．０〜１．６％とする。Mn Mn is added at low cost to enhance hardenability and improve toughness. If it is less than 0.5%, the effect is not obtained. On the other hand, if it exceeds 2.0%, weldability is impaired and delayed fracture is liable to occur. Preferably, it is set to 1.0 to 1.6%.
【００２２】Ｃｒ Ｃｒは、低コストで焼入れ性を向上させるため添加す
る。０．１％未満ではその効果が十分でなく、一方、
２．０％を超えると溶接性および靭性を損なうため、
０．１〜２．０％とする。好ましくは０．２〜１．５％
とする。Cr Cr is added to improve hardenability at low cost. If it is less than 0.1%, the effect is not enough, while
If it exceeds 2.0%, the weldability and toughness are impaired.
0.1 to 2.0%. Preferably 0.2-1.5%
And
【００２３】Ｔｉ Ｔｉは鋼中のＮと化合し、Ｎを固定して、Ｂによる焼入
れ性を確保するため、さらに、ＴｉＣの分散析出により
耐摩耗性の向上を導くため添加する。０．００５％未満
ではその効果が十分でなく、一方、０．５％を超えると
製品コストが上昇するため、０．００５〜０．５％とす
る。Ti Ti is added in order to combine with N in the steel and fix N to secure hardenability by B, and to further improve wear resistance by dispersing and depositing TiC. If the content is less than 0.005%, the effect is not sufficient. On the other hand, if the content exceeds 0.5%, the product cost increases.
【００２４】Ｂ Ｂは、微量で焼入れ性を高めるため添加する。０．００
０５％未満ではその効果が得られず、一方、０．００５
％を超えると溶接性を低下させ、却って焼入れ性を低下
させるため、０．０００５〜０．００５％とする。BB is added in a very small amount to enhance hardenability. 0.00
At less than 05%, the effect cannot be obtained.
%, The weldability is reduced, and the hardenability is rather reduced.
【００２５】Ａｌ Ａｌは、製鋼時の脱酸材として作用するため添加する。
０．００５％未満ではその効果が得られず、一方、０．
１０％を超えると靭性が低下するため、０．００５〜
０．１０％とする。好ましくは０．０１５〜０．０３５
％とする。Al Al is added because it acts as a deoxidizer during steelmaking.
If the content is less than 0.005%, the effect cannot be obtained.
If it exceeds 10%, the toughness is reduced.
0.10%. Preferably 0.015 to 0.035
%.
【００２６】Ｎ Ｎは、ＢとＢＮを形成し、焼入れ性を低下させる。Ｎ含
有量が０．００５％を超えると、本発明範囲内のＴｉ量
ではＮの固定が不十分となるため、０．００５％以下と
する。NN forms B and BN and lowers the hardenability. If the N content exceeds 0.005%, the amount of Ti within the range of the present invention is insufficient to fix N. Therefore, the N content is set to 0.005% or less.
【００２７】本発明の基本成分組成は以上であるが、更
にその特性を向上させる場合、Ｃｕ，Ｎｉ，Ｍｏ，Ｖ，
Ｎｂの一種または二種以上を添加することが可能であ
る。The basic component composition of the present invention is as described above. To further improve the characteristics, Cu, Ni, Mo, V,
One or two or more types of Nb can be added.
【００２８】Ｃｕ Ｃｕは、焼入れ性を向上させるため添加する。０．１％
未満ではその効果が得られず、１．０％を超えると熱間
脆性を生じるため、０．１〜１．０％とする。好ましく
は０．１〜０．３％とする。Cu Cu is added to improve hardenability. 0.1%
If it is less than 1.0%, the effect cannot be obtained, and if it exceeds 1.0%, hot embrittlement occurs, so the content is made 0.1 to 1.0%. Preferably, it is 0.1 to 0.3%.
【００２９】Ｎｉ Ｎｉは、靭性と焼入れ性を向上させるために添加する。
０．１％未満ではその効果が得られず、１．０％を超え
ると製品価格が上昇するため、０．１〜１．０％とす
る。好ましくは０．１〜０．３％とする。Ni Ni is added to improve toughness and hardenability.
If it is less than 0.1%, the effect cannot be obtained, and if it exceeds 1.0%, the product price increases. Preferably, it is 0.1 to 0.3%.
【００３０】Ｍｏ Ｍｏは、焼入れ性を向上させるため添加する。０．１％
未満ではその効果が得られず、１．０％を超えると溶接
性および靭性を低下させるため、０．１〜１．０％とす
る。好ましくは０．１〜０．５％とする。Mo Mo is added to improve hardenability. 0.1%
If it is less than 1.0%, the effect cannot be obtained, and if it exceeds 1.0%, the weldability and toughness are reduced. Preferably it is 0.1-0.5%.
【００３１】Ｖ Ｖは、析出硬化により、鋼材を硬化させるため添加す
る。０．０１％未満ではその効果が得られず、０．２％
を超えると溶接性を低下させるため、０．０１〜０．２
％とする。好ましくは０．０１〜０．１％とする。V V is added to harden the steel material by precipitation hardening. If less than 0.01%, the effect cannot be obtained, and 0.2%
Exceeds 0.01 to 0.2 to decrease the weldability.
%. Preferably, it is 0.01 to 0.1%.
【００３２】Ｎｂ Ｎｂは、圧延時の再結晶を抑制し、圧延によるオーステ
ナイト粒の展伸を容易にし、靭性を向上させる。０．０
０５％未満ではその効果が十分得られず、一方、０．１
％を超えると溶接性が低下するため、０．００５〜０．
１％とする。好ましくは０．００５〜０．０３％とす
る。Nb Nb suppresses recrystallization during rolling, facilitates expansion of austenite grains by rolling, and improves toughness. 0.0
If the content is less than 0.05%, the effect cannot be sufficiently obtained.
%, The weldability is reduced.
1%. Preferably it is 0.005 to 0.03%.
【００３３】２．ミクロ組織 旧オーステナイト粒展伸度（ｄＬ／ｄＺ）：２以上の焼
戻しマルテンサイト組織 但し、ｄＺ：鋼の肉厚方向の旧オーステナイト粒径、ｄ
Ｌ：鋼の圧延方向の旧オーステナイト粒径 本発明鋼では、目的とする硬度（ブリネル硬さＨＢ（１
０／３０００）：硬度３００以上）を得るため、焼戻し
マルテンサイト組織とし、旧オーステナイト粒展伸度
は、優れた靭性を得るため、２以上とする。2. Microstructure Previous austenite grain elongation (dL / dZ): tempered martensite structure of 2 or more, where dZ: old austenite grain size in the thickness direction of steel, d
L: Old austenite grain size in the rolling direction of the steel In the steel of the present invention, the target hardness (Brinell hardness HB (1
0/3000): a tempered martensite structure to obtain a hardness of 300 or more), and a prior austenite grain elongation of 2 or more to obtain excellent toughness.
【００３４】図１は、本発明範囲内の組成である、質量
％で、Ｃ：０．２３％，Ｓｉ：０．４５％、Ｍｎ：１．
５５％，Ｐ：０．０１１％，Ｓ：０．００５％、Ｃｒ：
０．３１％，Ｔｉ：０．０１８％、Ｂ：０．００１９
％，Ａｌ：０．０３５％、Ｎ：０．００２９％，残部が
実質的に鉄及び不可避不純物よりなる鋼を、種々の条件
で圧延した後、焼戻しマルテンサイト組織とした鋼板を
用い、吸収エネルギー値、ブリネル硬さに及ぼす旧オー
ステナイト粒伸展度の影響を調査した結果を示すもので
ある。FIG. 1 shows a composition within the range of the present invention, in terms of mass%, C: 0.23%, Si: 0.45%, Mn: 1.
55%, P: 0.011%, S: 0.005%, Cr:
0.31%, Ti: 0.018%, B: 0.0019
%, Al: 0.035%, N: 0.0029%, the balance being substantially composed of iron and unavoidable impurities, rolled under various conditions, and then using a steel sheet having a tempered martensitic structure, using a steel plate having absorbed energy. 4 shows the results of an investigation into the effect of the prior austenite grain elongation on the value and Brinell hardness.
【００３５】図より、旧オーステナイト粒展伸度が、２
以上の場合、優れた靭性が得られている。また、ブリネ
ル硬さは、旧オーステナイト粒展伸度によらず約３５０
〜４００で優れた耐摩耗性が得られる値となっている。From the figure, it can be seen that the old austenite grain elongation is 2
In the above cases, excellent toughness is obtained. The Brinell hardness is about 350 regardless of the former austenite grain elongation.
A value of ~ 400 gives excellent wear resistance.
【００３６】尚、旧オーステナイト粒の展伸度は、鋼材
の肉厚方向に沿う断面および鋼材の圧延方向に沿う断面
での旧オーステナイト粒の粒径比として求められ、例え
ば、日本工業規格ＪＩＳ Ｇ ０５５１に規定された焼
入れ焼戻し法による熱処理粒度試験法により求められ
る。The elongation degree of the prior austenite grains is obtained as a particle size ratio of the prior austenite grains in a cross section along the thickness direction of the steel material and a cross section along the rolling direction of the steel material. For example, Japanese Industrial Standard JIS G It is determined by a heat treatment particle size test method by a quenching and tempering method specified in 0551.
【００３７】ブリネル硬さは、ＪＩＳ Ｚ ２２４３に
よる、鋼板表面に直径１０ｍｍの圧子を押し込んだとき
に形成されるくぼみの直径を測定するブリネル硬さ（Ｈ
Ｂ（１０／３０００））試験により求めた。The Brinell hardness is measured according to JIS Z 2243 to measure the diameter of a depression formed when a 10 mm diameter indenter is pressed into the surface of a steel sheet.
B (10/3000)).
【００３８】吸収エネルギーはシャルピー衝撃試験を試
験温度ー４０℃で、３本の試験片で行ない、その平均値
を求め、ｖＥ−４０℃：１７Ｊ以上を本発明の目標値と
した。試験片は、ＪＩＳ Ｚ ２２０２に記載の１０×
１０（ｍｍ），２ｍｍＶノッチとし、採取位置は板厚中
央、採取方向は圧延方向とした。As for the absorbed energy, a Charpy impact test was conducted at a test temperature of -40.degree. C. on three test pieces, and the average value was determined. A target value of vE-40.degree. The test piece was a 10 × described in JIS Z 2202.
The notch was 10 (mm), 2 mm V, the sampling position was the center of the plate thickness, and the sampling direction was the rolling direction.
【００３９】３．製造条件 本発明鋼は、オーステナイト未再結晶域で強圧下後、直
接焼入れ、焼戻しにより製造することが好ましい。好適
製造条件について説明する。3. Manufacturing Conditions The steel of the present invention is preferably manufactured by direct quenching and tempering after being strongly pressed in the austenite unrecrystallized region. Preferred manufacturing conditions will be described.
【００４０】熱間圧延 鋼片を加熱後、熱間圧延を行う。加熱温度は、９５０℃
未満では、鋼の変形抵抗が高くなり、一方、１２５０℃
を超えると、粗大粒となり、強度および靭性の確保が困
難となるため、９５０〜１２５０℃とするのが好まし
い。Hot Rolling After the steel slab is heated, hot rolling is performed. Heating temperature is 950 ℃
Below, the deformation resistance of the steel increases, while 1250 ° C.
If it exceeds 950, it becomes coarse, and it is difficult to ensure strength and toughness.
【００４１】熱間圧延において、９００℃以下のオース
テナイト未再結晶域において累積圧下率５０％以上の圧
延を行う。In the hot rolling, rolling is performed at a cumulative draft of 50% or more in an austenite unrecrystallized region at 900 ° C. or less.
【００４２】旧オーステナイト粒の展伸度を２以上と
し、その形状を保持するため、オーステナイト未再結晶
域で且つ９００℃以下の低温側、好ましくは８５０℃〜
Ａｒ3で、累積圧下率を５０％以上とする圧延を行う。In order to maintain the shape of the prior austenite grains at a degree of elongation of 2 or more and maintain the shape thereof, the austenite is in the non-recrystallized region and at a low temperature of 900 ° C. or less, preferably 850 ° C.
Rolling is performed with Ar3 to reduce the cumulative draft to 50% or more.
【００４３】図２に旧オーステナイト粒の展伸度におよ
ぼす９００℃以下での累積圧下率の影響を示す。累積圧
下率５０％以上とした場合、旧オーステナイト粒は展伸
度２以上になる。図３に鋼材の靭性（シャルピー吸収エ
ネルギー値）と耐摩耗性（ブリネル硬さ）に及ぼす９０
０℃以下の累積圧下率の影響を示す。FIG. 2 shows the effect of the cumulative rolling reduction at 900 ° C. or less on the elongation of the prior austenite grains. When the cumulative rolling reduction is 50% or more, the austenite grains have an elongation of 2 or more. FIG. 3 shows the effect of 90 on the toughness (Charpy absorbed energy value) and wear resistance (Brinell hardness) of steel materials.
This shows the effect of the cumulative rolling reduction below 0 ° C.
【００４４】旧オーステナイト粒の展伸度が２以上とな
るように、累積圧下率を５０％以上とした場合、図１と
同様の本発明の効果が得られている。供試鋼、試験方法
および靭性、耐摩耗性の評価は、図１に準じて行った。When the cumulative rolling reduction is 50% or more so that the austenite grains have an elongation of 2 or more, the effect of the present invention similar to that of FIG. 1 is obtained. The test steel, the test method, and the evaluation of toughness and wear resistance were performed according to FIG.
【００４５】熱処理 熱間圧延後、直ちにＡｒ3点以上から焼入れし、その後
３００℃〜Ａｃ1で焼戻し未再結晶域における累積圧下
の効果を失わないように、圧延後、直ちに、焼き入れを
行う。焼入れ開始温度は、マルテンサイト単相組織とす
るためＡｒ3以上とし、オーステナイト単相組織より焼
入れを行う。Heat treatment After the hot rolling, quenching is performed immediately from the Ar3 point or higher, and then quenching is performed immediately after the rolling so that the effect of the cumulative reduction in the non-recrystallized region at 300 ° C. to Ac1 is maintained. The quenching start temperature is Ar3 or more in order to obtain a martensite single phase structure, and quenching is performed from an austenitic single phase structure.
【００４６】焼入れ停止温度は、マルテンサイト組織と
するため、Ｍs点以下とすることが望ましく、冷却速度
は水焼入れなどにより、２０℃／ｓ以上とすることが望
ましい。The quenching stop temperature is desirably equal to or lower than the Ms point to obtain a martensite structure, and the cooling rate is desirably equal to or higher than 20 ° C./s by water quenching or the like.
【００４７】Ａｒ3点、Ｍs点は例えば、以下の式により
求めることができる。The Ar3 point and the Ms point can be obtained, for example, by the following equations.
【００４８】Ａｒ3（℃）＝９１０−３１０Ｃ−８０Ｍ
ｎ−２０Ｃｕ−１５Ｃｒ−５５Ｎｉ−８０Ｍｏ、但し、
各元素は質量％とする。Ar 3 (° C.) = 910-310C-80M
n-20Cu-15Cr-55Ni-80Mo, provided that
Each element is defined as mass%.
【００４９】Ｍs（℃）＝５１７−３００Ｃ−３３Ｍｎ
−２２Ｃｒ−１７Ｎｉ−１１Ｍｏ−１１Ｓｉ、但し、各
元素は質量％とする。Ms (° C.) = 517-300C-33Mn
-22Cr-17Ni-11Mo-11Si, where each element is mass%.
【００５０】焼入れ後、焼戻しを３００℃〜Ａｃ1で行
う。３００℃未満では、靭性が向上せず、一方、焼戻し
温度をＡｃ1点以上とすると硬度低下が著しく、本発明
が目的とする硬度が得られない。好ましくは３００〜６
５０℃とする。Ａｃ1点は例えば、Ａｃ1（℃）＝７２３
−１４Ｍｎ＋２２Ｓｉ−１４．４Ｎｉ＋２３．３Ｃｒに
より求めることができる。After quenching, tempering is performed at 300 ° C. to Ac1. If the temperature is lower than 300 ° C., the toughness is not improved. On the other hand, if the tempering temperature is higher than the Ac1 point, the hardness is significantly reduced, and the hardness targeted by the present invention cannot be obtained. Preferably 300 to 6
50 ° C. The Ac1 point is, for example, Ac1 (° C.) = 723
-14Mn + 22Si-14.4Ni + 23.3Cr.
【００５１】図４は、９００℃以下の累積圧下率を３５
％、７０％とした直接焼入れ焼戻し鋼板の靭性と硬度に
及ぼす焼戻し温度の影響を示すもので、累積圧下率７０
％とした鋼板では、焼戻し温度３００℃以上で優れた靭
性が得られが、Ａｃ1点以上においては本発明が目的と
する硬度が得られない。FIG. 4 shows that the cumulative rolling reduction under 900 ° C. is 35%.
% And 70% indicate the effect of the tempering temperature on the toughness and hardness of the direct quenched and tempered steel sheet.
%, Excellent toughness can be obtained at a tempering temperature of 300 ° C. or higher, but the desired hardness of the present invention cannot be obtained at an Ac1 point or higher.
【００５２】累積圧下率が３５％の鋼板では、焼戻し温
度３００℃以上でも靭性の改善は認められない。尚、焼
入れ停止温度と焼戻し温度は、本発明が目的とする硬度
が得られる範囲内で、靭性を改善させるため高温とする
ことが望ましい。With a steel sheet having a cumulative reduction of 35%, no improvement in toughness is observed even at a tempering temperature of 300 ° C. or higher. The quenching stop temperature and the tempering temperature are desirably set to high temperatures in order to improve the toughness within a range in which the hardness targeted by the present invention can be obtained.
【００５３】[0053]
【実施例】[実施例１]表１に供試鋼Ａ〜Ｇの化学成分
を、表２に製造条件および得られた鋼板のミクロ組織お
よび硬度、靭性を示す。供試鋼は板厚２０〜１００ｍｍ
の鋼板とした。EXAMPLES Example 1 Table 1 shows the chemical components of the test steels A to G, and Table 2 shows the production conditions and the microstructure, hardness and toughness of the obtained steel sheet. The test steel is 20 to 100 mm thick
Steel plate.
【００５４】組織観察は、光学顕微鏡により行ない、旧
オーステナイト粒の展伸度は、日本工業規格ＪＩＳ Ｇ
０５５１に規定された焼入れ焼戻し法による熱処理粒
度試験法により現出させたオーステナイト粒について鋼
材の肉厚方向に沿う断面および鋼材の圧延方向に沿う断
面での粒径比として求めた。硬度およびシャルピー衝撃
試験は、図１に準拠して行った。The structure was observed with an optical microscope, and the degree of elongation of the former austenite grains was determined according to Japanese Industrial Standard JIS G
The austenitic grains revealed by the heat treatment grain size test method according to the quenching and tempering method specified in 0551 were determined as the grain size ratio in the cross section along the thickness direction of the steel material and the cross section along the rolling direction of the steel material. The hardness and Charpy impact tests were performed according to FIG.
【００５５】表２中、実施例１〜６は、本発明例であ
り、いずれもブリネル硬さは３００以上、靭性は−４０
℃の吸収エネルギーで１７Ｊを大幅に上回る良好な値
で、優れた耐摩耗性と靭性が得られている。In Table 2, Examples 1 to 6 are examples of the present invention, each having a Brinell hardness of 300 or more and a toughness of -40.
Excellent abrasion resistance and toughness are obtained at a good value significantly exceeding 17 J at an absorption energy of ° C.
【００５６】比較例１〜３は、旧オーステナイト粒展伸
度が２未満の焼戻しマルテンサイト組織で、ブリネル硬
さは３００以上であるが、靭性が劣っている。Comparative Examples 1 to 3 have a tempered martensite structure in which the prior austenite grain elongation is less than 2 and have a Brinell hardness of 300 or more, but are inferior in toughness.
【００５７】比較例４は、旧オーステナイト粒展伸度が
２以上の焼き入れままのマルテンサイト組織であり、耐
摩耗性は良好であるが、靭性に劣っている。Comparative Example 4 has an as-quenched martensite structure having a prior austenite grain elongation of 2 or more, and has good wear resistance but poor toughness.
【００５８】比較例５は、Ｃ量が本発明範囲外である供
試鋼Ｇによるもので、旧オーステナイト粒展伸度が２以
上の焼戻しマルテンサイト組織で、靭性は−４０℃の吸
収エネルギーで１７Ｊ以上と優れているが、ブリネル硬
さは１５０で耐摩耗性が劣っている。Comparative Example 5 is based on test steel G having a C content outside the range of the present invention, and has a tempered martensite structure having a prior austenite grain elongation of 2 or more, and has a toughness at an absorption energy of -40 ° C. It is excellent at 17 J or more, but has a Brinell hardness of 150 and poor wear resistance.
【００５９】比較例６は、焼入れ停止温度を、鋼種Ｄの
Ｍｓ点を超える５５０℃としたもので、旧オーステナイ
ト粒展伸度は２以上であるが、焼戻しベイナイト組織で
あり、靭性は良好なもののブリネル硬さは２２３と耐摩
耗性が大幅に低下している。In Comparative Example 6, the quenching stop temperature was set to 550 ° C. exceeding the Ms point of steel type D, and the austenite grain elongation was 2 or more, but it had a tempered bainite structure and good toughness. However, the Brinell hardness was 223, and the wear resistance was significantly reduced.
【００６０】比較例７は、再加熱焼入れ処理によるもの
で、ブリネル硬さは４１２と耐摩耗性は良好であった
が、圧延後、展伸していた旧オーステナイト粒が、再加
熱されることにより、展伸度が１．３となり、−４０℃
の吸収エネルギーが１６Ｊと大幅に低下している。Comparative Example 7 was a result of reheating and quenching, in which the Brinell hardness was 412 and the abrasion resistance was good, but the old austenite grains that had expanded after rolling were reheated. , The elongation becomes 1.3, -40 ° C
Has a significantly reduced absorption energy of 16J.
【００６１】[0061]
【表１】 [Table 1]
【００６２】[0062]
【表２】 [Table 2]
【００６３】[実施例２]実施例１と同様に、表１に示す
供試鋼Ａ〜Ｇを用い、板厚２０〜１００ｍｍの鋼板とし
た。[Example 2] In the same manner as in Example 1, the test steels A to G shown in Table 1 were used to form steel plates having a thickness of 20 to 100 mm.
【００６４】表３に製造条件および得られた鋼板のミク
ロ組織および硬度、靭性を示す。硬度、靭性は、実施例
１と同様の方法により評価を行った。Table 3 shows the manufacturing conditions and the microstructure, hardness and toughness of the obtained steel sheet. Hardness and toughness were evaluated in the same manner as in Example 1.
【００６５】表３中、実施例１〜６は、本発明例であ
り、いずれもブリネル硬さは３００以上、靭性は−４０
℃の吸収エネルギーで１７Ｊを大幅に上回る良好な値
で、優れた耐摩耗性と靭性が得られている。In Table 3, Examples 1 to 6 are Examples of the present invention, each having a Brinell hardness of 300 or more and a toughness of -40.
Excellent abrasion resistance and toughness are obtained at a good value significantly exceeding 17 J at an absorption energy of ° C.
【００６６】比較例１は、９００℃以下の累積圧下率を
５０％未満とし、且つ、焼戻し温度を２５０℃としたも
ので、ブリネル硬さは３００以上で耐摩耗性は良好であ
るが、−４０℃の吸収エネルギーが１７Ｊ以下と靭性に
劣っている。In Comparative Example 1, the cumulative draft at 900 ° C. or less was less than 50%, and the tempering temperature was 250 ° C. The Brinell hardness was 300 or more and the wear resistance was good. The absorption energy at 40 ° C. is 17 J or less, which is poor in toughness.
【００６７】比較例２は、焼戻し温度が３００℃で、９
００℃以下の累積圧下率が５０％未満であり、ブリネル
硬さが３５８と耐摩耗性は良好であるが、−４０℃の吸
収エネルギーが１２Ｊと著しく靭性が劣化している。In Comparative Example 2, the tempering temperature was 300 ° C.
Although the cumulative draft at 00 ° C or less is less than 50% and the Brinell hardness is 358, the wear resistance is good, but the absorption energy at −40 ° C. is 12 J, and the toughness is significantly deteriorated.
【００６８】比較例３は、焼戻しを行わなかったもの
で、ブリネル硬さは３００以上で耐摩耗性は良好である
が、−４０℃の吸収エネルギーが１７Ｊ未満で、著しく
靭性が劣化している。Comparative Example 3 was not subjected to tempering and had a Brinell hardness of 300 or more and good abrasion resistance. However, the absorption energy at -40 ° C. was less than 17 J, and the toughness was remarkably deteriorated. .
【００６９】比較例４は、焼戻し温度が２００℃で、ブ
リネル硬さは３００以上で耐摩耗性は良好であるが、−
４０℃の吸収エネルギーが１７Ｊを大幅に下回り、著し
く靭性が劣化している。In Comparative Example 4, the tempering temperature was 200 ° C., the Brinell hardness was 300 or more, and the wear resistance was good.
The absorbed energy at 40 ° C. is significantly lower than 17 J, and the toughness is significantly deteriorated.
【００７０】比較例５は、Ｃ量が本発明範囲外である供
試鋼Ｇによるもので、靭性は−４０℃の吸収エネルギー
で１７Ｊを大幅に上回り、優れているが、ブリネル硬さ
は１５０で耐摩耗性が劣っている。Comparative Example 5 is based on test steel G having a C content outside the range of the present invention. The toughness is significantly higher than 17 J at an energy absorption of -40 ° C., and the Brinell hardness is 150. And inferior wear resistance.
【００７１】比較例６は、焼入れ停止温度を、鋼種Ｄの
Ｍｓ点を超える５５０℃としたもので、焼戻しベイナイ
ト組織であり、靭性は良好なもののブリネル硬さは２２
３と耐摩耗性が大幅に低下している。In Comparative Example 6, the quenching stop temperature was 550 ° C. exceeding the Ms point of steel type D, which had a tempered bainite structure and good toughness, but had a Brinell hardness of 22.
3 and the wear resistance is significantly reduced.
【００７２】比較例７は、再加熱焼入れ処理によるもの
で、ブリネル硬さは４１２と耐摩耗性は良好であった
が、圧延後、展伸していた旧オーステナイト粒が、再加
熱されることにより、展伸度が１．３となり、−４０℃
の吸収エネルギーが１６Ｊと大幅に低下している。Comparative Example 7 was a result of a reheating quenching treatment, in which the Brinell hardness was 412 and the wear resistance was good, but the old austenite grains that had been expanded after rolling were reheated. , The elongation becomes 1.3, -40 ° C
Has a significantly reduced absorption energy of 16J.
【００７３】[0073]
【表３】 [Table 3]
【００７４】[0074]
【発明の効果】本発明によれば、旧オーステナイト粒径
を伸展させた焼戻しマルテンサイト組織を有し、靭性に
優れた耐摩耗鋼および生産性に優れたその製造方法が得
られ、土木機械、産業機械等の信頼性や施工性が向上
し、産業上極めて有用である。According to the present invention, it is possible to obtain a wear-resistant steel having a tempered martensite structure in which the prior austenite grain size is extended and having excellent toughness and a method for producing the same having excellent productivity. The reliability and workability of industrial machines and the like are improved, and they are extremely useful in industry.
【図１】耐摩耗性（表面ブリネル硬さ）、靭性（−４０
℃における吸収エネルギー）に及ぼす旧オーステナイト
粒展伸度の影響を示す図。FIG. 1 Abrasion resistance (surface Brinell hardness), toughness (−40)
FIG. 2 is a graph showing the influence of the prior austenite grain elongation on the absorption energy at ℃.
【図２】旧オーステナイト粒展伸度に及ぼす累積圧下率
の影響を示す図。FIG. 2 is a graph showing the influence of the cumulative rolling reduction on the prior austenite grain elongation.
【図３】耐摩耗性（表面ブリネル硬さ）、靭性（−４０
℃における吸収エネルギー）に及ぼす累積圧下率の影響
を示す図。FIG. 3 shows wear resistance (surface Brinell hardness) and toughness (−40)
FIG. 3 is a diagram showing the effect of the cumulative rolling reduction on the energy absorbed at ℃.
【図４】耐摩耗性（表面ブリネル硬さ）、靭性（−４０
℃における吸収エネルギー）に及ぼす焼戻し温度の影響
を示す図。FIG. 4 shows abrasion resistance (surface Brinell hardness) and toughness (−40)
The figure which shows the influence of the tempering temperature on (energy absorbed in ° C).
───────────────────────────────────────────────────── フロントページの続き Ｆターム(参考） 2D015 JA06 4K032 AA01 AA02 AA04 AA05 AA11 AA12 AA16 AA21 AA31 AA35 BA01 CA02 CB02 CC03 CD03 ──────────────────────────────────────────────────の Continued on the front page F term (reference) 2D015 JA06 4K032 AA01 AA02 AA04 AA05 AA11 AA12 AA16 AA21 AA31 AA35 BA01 CA02 CB02 CC03 CD03
Claims (4)
量％で、Ｃ：０．０５〜０．４０％、Ｓｉ：０．１〜
０．８％、Ｍｎ：０．５〜２．０％、Ｃｒ：０．１〜
２．０％、Ｔｉ：０．００５〜０．５％、Ｂ：０．００
０５〜０．００５％、Ａｌ：０．００５〜０．１０％、
Ｎ：０．００５％以下、残部実質的にＦｅおよび不可避
不純物とからなる耐摩耗鋼。 （１）旧オーステナイト粒展伸度（ｄＬ／ｄＺ）：２以
上の焼戻しマルテンサイト組織 但し、ｄＺ：鋼の肉厚方向の旧オーステナイト粒径、ｄ
Ｌ：鋼の圧延方向の旧オーステナイト粒径C .: 0.05 to 0.40%, Si: 0.1 to 100% by mass characterized by having the following structure:
0.8%, Mn: 0.5 to 2.0%, Cr: 0.1 to
2.0%, Ti: 0.005 to 0.5%, B: 0.00
05-0.005%, Al: 0.005-0.10%,
N: a wear-resistant steel consisting of 0.005% or less, with the balance substantially consisting of Fe and unavoidable impurities. (1) Old austenite grain elongation (dL / dZ): tempered martensite structure of 2 or more, where dZ: old austenite grain size in the thickness direction of steel, d
L: Old austenite grain size in the rolling direction of steel
０．１〜１．０％、Ｎｉ：０．１〜１．０％、Ｍｏ：
０．１〜１．０％、Ｖ：０．０１〜０．２％の一種また
は二種以上を含有する請求項１記載の耐摩耗鋼。2. The steel composition further comprises Cu:
0.1-1.0%, Ni: 0.1-1.0%, Mo:
The wear-resistant steel according to claim 1, containing one or more of 0.1 to 1.0% and V: 0.01 to 0.2%.
０．００５〜０．１％を含有する請求項１または２記載
の耐摩耗鋼。3. The steel composition further comprises Nb:
3. The wear-resistant steel according to claim 1, comprising 0.005 to 0.1%.
有する鋼を、９００℃以下のオーステナイト未再結晶域
において累積圧下率５０％以上で熱間圧延後、直ちにＡ
ｒ3点以上から焼入れし、その後３００℃〜Ａｃ1で焼戻
しすることを特徴とする耐摩耗鋼の製造方法。4. A steel having the composition according to claim 1 is hot rolled immediately after hot rolling at a cumulative rolling reduction of 50% or more in an austenite unrecrystallized region at 900 ° C. or less.
A method for producing wear-resistant steel, characterized by quenching from r3 or more and then tempering at 300 ° C. to Ac1.
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|---|---|---|---|
| JP2000205313A JP2002020837A (en) | 2000-07-06 | 2000-07-06 | Wear resistant steel excellent in toughness and its production method |
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| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2000205313A JP2002020837A (en) | 2000-07-06 | 2000-07-06 | Wear resistant steel excellent in toughness and its production method |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JP2002020837A true JP2002020837A (en) | 2002-01-23 |
Family
ID=18702422
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|---|---|---|---|
| JP2000205313A Pending JP2002020837A (en) | 2000-07-06 | 2000-07-06 | Wear resistant steel excellent in toughness and its production method |
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| Country | Link |
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| JP (1) | JP2002020837A (en) |
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