JPH0686643B2 - Method for producing high hardness wear-resistant steel with HB ≧ 500 excellent in delayed cracking resistance after welding - Google Patents
Method for producing high hardness wear-resistant steel with HB ≧ 500 excellent in delayed cracking resistance after weldingInfo
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- JPH0686643B2 JPH0686643B2 JP59097461A JP9746184A JPH0686643B2 JP H0686643 B2 JPH0686643 B2 JP H0686643B2 JP 59097461 A JP59097461 A JP 59097461A JP 9746184 A JP9746184 A JP 9746184A JP H0686643 B2 JPH0686643 B2 JP H0686643B2
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Description
【発明の詳細な説明】 （産業上の利用分野） 本発明は溶接後の耐遅れ割れ性に優れたHB≧500の高硬
度耐摩耗鋼の製造方法に関するものである。TECHNICAL FIELD The present invention relates to a method for producing a high hardness wear resistant steel with H B ≧ 500 which is excellent in delayed crack resistance after welding.
（従来の技術） 建設機械（ブルドーザー）排土板、排泥管、ダンプトラ
ックベッセル等の耐摩耗性が必要とされる部材用の耐摩
耗鋼として、従来特公昭50−22968号公報において、C:
0.18〜0.30％、Si:0.10〜0.70％、Mn:1.1〜2.0％、Cr:
0.3〜1.5％、Mo:0.05〜0.35％、V:0.01〜0.15％、Al:0.
01〜0.10％を含む鋼が提案されている。また、特公昭46
−2612号公報においてはC:0.30〜1.0％、Si:0.05〜1.5
％、Mn:0.2〜2.0％、Mo:1.0％以下、Ti:0.20〜2.0％、C
r:0.5〜10.0％、残部Feからなる高Cr−Mo−Ti系の低合
金鋼が提案されている。(Prior Art) As a wear-resistant steel for a construction machine (bulldozer) such as an earth plate, a mud pipe, a dump truck vessel and the like, which is required to have wear resistance, in Japanese Patent Publication No. 50-22968, C :
0.18 ~ 0.30%, Si: 0.10 ~ 0.70%, Mn: 1.1 ~ 2.0%, Cr:
0.3-1.5%, Mo: 0.05-0.35%, V: 0.01-0.15%, Al: 0.
Steels containing 01-0.10% have been proposed. In addition, Japanese Examined Sho 46
In the −2612 publication, C: 0.30 to 1.0%, Si: 0.05 to 1.5
%, Mn: 0.2 to 2.0%, Mo: 1.0% or less, Ti: 0.20 to 2.0%, C
A high Cr-Mo-Ti low alloy steel composed of r: 0.5 to 10.0% and the balance Fe is proposed.
しかしながら、これ等の耐摩耗鋼は溶接性、特に溶接後
の耐遅れ割れ性（遅れ割れとは別名低温割れとも称し、
溶接時に侵入した水素による遅れ割れのことである。）
を評価するPH値に対しての考慮は払われておらず、特に
後者においては比較的多量の合金元素を添加している関
係でコスト高となり、省資源的な観点からも問題があ
る。However, these wear-resistant steels have weldability, in particular, delayed crack resistance after welding (delayed crack is also known as cold crack,
It is a delayed crack due to hydrogen that entered during welding. )
Considering the relative P H value to evaluate is not paid, particularly the latter becomes costly in relation that the addition of relatively large amounts of alloying elements in, there is also a problem from the resource saving standpoint.
（発明が解決しようとする課題） 近年、エネルギー資源の涸渇等に起因して、より安価で
かつ高品質な耐摩耗鋼が要求されて来ている。(Problems to be Solved by the Invention) In recent years, due to depletion of energy resources and the like, there has been a demand for more inexpensive and high-quality wear-resistant steel.
本発明はかかる現況に鑑みて、前記した溶接後の耐遅れ
割れ性に優れ、耐久性に富みしかも省資源的要求を満足
する安価なHB≧500の高硬度耐摩耗鋼を製造する方法を
提供することを目的とするものである。In view of the present situation, the present invention provides a method for producing an inexpensive H B ≧ 500 high hardness wear-resistant steel which is excellent in delayed cracking resistance after welding, rich in durability, and satisfies the resource saving requirement. It is intended to be provided.
（課題を解決するための手段） 本発明者らは、溶接後の耐遅れ割れ性に優れたHB≧500
の高硬度耐摩耗鋼の製造方法を提供すべく種々の研究実
験を重ねた結果、高硬度耐摩耗鋼の溶接後の耐遅れ割れ
性を向上させるには、溶接時に侵入する水素による遅れ
割れに対する炭素当量は重回帰法で求めた次式で示すPH
が1.0％以下となることが肝要であることを知見した。(Means for Solving the Problems) The present inventors have found that H B ≧ 500, which is excellent in delayed crack resistance after welding.
As a result of various researches and experiments to provide a method for manufacturing high hardness wear-resistant steel, in order to improve the delayed crack resistance of high hardness wear-resistant steel after welding, P H carbon equivalent represented by the following formula obtained by the multiple regression method
It was found that it is important that the ratio be 1.0% or less.
PH＝Ｃ＋Mn/10＋Mo/6＋Cr/15＋3V＋40P＋100B(%) 本発明はかかる知見にもとづき、さらにＰがPH値を大き
くする有害な元素であることを考慮した上で、最も廉価
となる鋼材の成分系を鋭意検討し、溶接後の耐遅れ割れ
性に優れたHB≧500の高硬度耐摩耗鋼の製造方法を開発
した。 P H = C + Mn / 10 + Mo / 6 + Cr / 15 + 3V + 40P + 100B (%) The present invention is based on this finding, in further P is taken into consideration that it is a harmful element which increases the P H value, component-based steel as the least expensive We have developed a method for manufacturing high hardness wear-resistant steel with H B ≧ 500 that has excellent delayed crack resistance after welding.
即ち、本発明の要旨とするところは下記のとおりであ
る。That is, the gist of the present invention is as follows.
（１）C:0.3〜0.5％、Si:0.05〜0.5％、Mn:0.5〜1.5
％、P:0.010％以下、S:0.005％以下、Cr:0.1〜1.0％、M
o:0.02〜0.4％、sol.Al:0.01〜0.1％、Ca:0.006％以下
を含み、残部鉄および不可避的不純物からなりかつ下記
式で示されるPH値が1.0％以下となる鋼を焼入れたまま
とするか、または焼入れた後、低温焼戻しすることを特
徴とする溶接後の耐遅れ割れ性に優れたHB≧500の高硬
度耐摩耗鋼の製造方法。(1) C: 0.3-0.5%, Si: 0.05-0.5%, Mn: 0.5-1.5
%, P: 0.010% or less, S: 0.005% or less, Cr: 0.1 to 1.0%, M
o: 0.02~0.4%, sol.Al: 0.01~0.1 %, Ca: include 0.006% or less, quenching the steel P H value indicated by the result and the following formula the balance iron and inevitable impurities is 1.0% or less A method for producing a high hardness wear-resistant steel with H B ≧ 500, which is excellent in delayed crack resistance after welding, characterized in that it is left as it is or is quenched and then tempered at a low temperature.
PH＝Ｃ＋Mn/10＋Mo/6＋Cr/15＋3V＋40P＋100B(%) （２）C:0.3〜0.5％、Si:0.05〜0.5％、Mn:0.5〜1.5
％、P:0.010％以下、S:0.005％以下、Cr:0.1〜1.0％、M
o:0.02〜0.4％、sol.Al:0.01〜0.1％、Ca:0.006％以
下、B:0.0005〜0.005％を含み、残部鉄および不可避的
不純物からなりかつ下記式で示されるPH値が1.0％以下
となる鋼を焼入れたままとするか、または焼入れた後、
低温焼戻しすることを特徴とする溶接後の耐遅れ割れ性
に優れたHB≧500の高硬度耐摩耗鋼の製造方法。 P H = C + Mn / 10 + Mo / 6 + Cr / 15 + 3V + 40P + 100B (%) (2) C: 0.3~0.5%, Si: 0.05~0.5%, Mn: 0.5~1.5
%, P: 0.010% or less, S: 0.005% or less, Cr: 0.1 to 1.0%, M
o: 0.02~0.4%, sol.Al: 0.01~0.1 %, Ca: 0.006% or less, B: comprises 0.0005 to 0.005%, P H value of 1.0 indicated by the result and the following formula the balance iron and unavoidable impurities % Steel or less, or after quenching,
A method for producing a high hardness wear resistant steel with H B ≧ 500 excellent in delayed cracking resistance after welding, characterized by low temperature tempering.
PH＝Ｃ＋Mn/10＋Mo/6＋Cr/15＋3V＋40P＋100B(%) （３）C:0.3〜0.5％、Si:0.05〜0.5％、Mn:0.5〜1.5
％、P:0.010％以下、S:0.005％以下、Cr:0.1〜1.0％、M
o:0.02〜0.4％、sol.Al:0.01〜0.1％、Ca:0.006％以
下、B:0.0005〜0.005％、Ti:0.005〜0.05％を含み、残
部鉄および不可避的不純物からなりかつ下記式で示され
るPH値が1.0％以下となる鋼を焼入れたままとするか、
または焼入れた後、低温焼戻しすることを特徴とする溶
接後の耐遅れ割れ性に優れたHB≧500の高硬度耐摩耗鋼
の製造方法。 P H = C + Mn / 10 + Mo / 6 + Cr / 15 + 3V + 40P + 100B (%) (3) C: 0.3~0.5%, Si: 0.05~0.5%, Mn: 0.5~1.5
%, P: 0.010% or less, S: 0.005% or less, Cr: 0.1 to 1.0%, M
o: 0.02-0.4%, sol.Al:0.01-0.1%, Ca: 0.006% or less, B: 0.0005-0.005%, Ti: 0.005-0.05%, the balance consists of iron and unavoidable impurities and or P H value shown is remains quenched steel comprising 1.0% or less,
Alternatively, a method for producing a high hardness wear-resistant steel with H B ≧ 500 excellent in delayed crack resistance after welding, characterized by quenching and then low-temperature tempering.
PH＝Ｃ＋Mn/10＋Mo/6＋Cr/15＋3V＋40P＋100B(%) （４）C:0.3〜0.5％、Si:0.05〜0.5％、Mn:0.5〜1.5
％、P:0.010％以下、S:0.005％以下、Cr:0.1〜1.0％、M
o:0.02〜0.4％、sol.Al:0.01〜0.1％、Ca:0.006％以
下、およびCu:0.5％以下、Ni:0.5％以下、Nb:0.05％以
下、V:0.05％以下の１種又は２種以上を含み、残部鉄お
よび不可避的不純物からなりかつ下記式で示されるPH値
が1.0％以下となる鋼を焼入れたままとするか、または
焼入れた後、低温焼戻しすることを特徴とする溶接後の
耐低温遅れ性に優れたHB≧500の高硬度耐摩耗鋼の製造
方法。 P H = C + Mn / 10 + Mo / 6 + Cr / 15 + 3V + 40P + 100B (%) (4) C: 0.3~0.5%, Si: 0.05~0.5%, Mn: 0.5~1.5
%, P: 0.010% or less, S: 0.005% or less, Cr: 0.1 to 1.0%, M
o: 0.02-0.4%, sol.Al:0.01-0.1%, Ca: 0.006% or less, and Cu: 0.5% or less, Ni: 0.5% or less, Nb: 0.05% or less, V: 0.05% or less, or comprises two or more, or P H value indicated by the result and the following formula the balance iron and unavoidable impurities to remain quenched steel to be 1.0% or less, or quenching after a feature that low-temperature tempering A method for manufacturing high hardness wear-resistant steel with H B ≧ 500, which has excellent low temperature lag resistance after welding.
PH＝Ｃ＋Mn/10＋Mo/6＋Cr/15＋3V＋40P＋100B(%) （５）C:0.3〜0.5％、Si:0.05〜0.5％、Mn:0.5〜1.5
％、P:0.010％以下、S:0.005％以下、Cr:0.1〜1.0％、M
o:0.02〜0.4％、sol.Al:0.01〜0.1％、Ca:0.006％以
下、B:0.0005〜0.005％、およびCu:0.5％以下、Ni:0.5
％以下、Nb:0.05％以下、V:0.05％以下の１種又は２種
以上を含み、残部鉄および不可避的不純物からなりかつ
下記式で示されるPH値が1.0％以下となる鋼を焼入れた
ままとするか、または焼入れた後、低温焼戻しすること
を特徴とする溶接後の耐遅れ割れ性に優れたHB≧500の
高硬度耐摩耗鋼の製造方法。 P H = C + Mn / 10 + Mo / 6 + Cr / 15 + 3V + 40P + 100B (%) (5) C: 0.3~0.5%, Si: 0.05~0.5%, Mn: 0.5~1.5
%, P: 0.010% or less, S: 0.005% or less, Cr: 0.1 to 1.0%, M
o: 0.02-0.4%, sol.Al:0.01-0.1%, Ca: 0.006% or less, B: 0.0005-0.005%, and Cu: 0.5% or less, Ni: 0.5
% Or less, Nb: 0.05% or less, V: include one or more than 0.05%, quenching the steel P H value indicated by the result and the following formula the balance iron and inevitable impurities is 1.0% or less A method for producing a high hardness wear-resistant steel with H B ≧ 500, which is excellent in delayed crack resistance after welding, characterized in that it is left as it is or is quenched and then tempered at a low temperature.
PH＝Ｃ＋Mn/10＋Mo/6＋Cr/15＋3V＋40P＋100B(%) （６）C:0.3〜0.5％、Si:0.05〜0.5％、Mn:0.5〜1.5
％、P:0.010％以下、S:0.005％以下、Cr:0.1〜1.0％、M
o:0.02〜0.4％、sol.Al:0.01〜0.1％、Ca:0.006％以
下、B:0.0005〜0.005％、Ti:0.005〜0.05％、およびCu:
0.5％以下、Ni:0.5％以下、Nb:0.05％以下、V:0.05％以
下の１種又は２種以上を含み、残部鉄および不可避的不
純物からなりかつ下記式で示されるPH値が1.0％以下と
なる鋼を焼入れたままとするか、または焼入れた後、低
温焼戻しすることを特徴とする溶接後の耐遅れ割れ性に
優れたHB≧500の高硬度耐摩耗鋼の製造方法。 P H = C + Mn / 10 + Mo / 6 + Cr / 15 + 3V + 40P + 100B (%) (6) C: 0.3~0.5%, Si: 0.05~0.5%, Mn: 0.5~1.5
%, P: 0.010% or less, S: 0.005% or less, Cr: 0.1 to 1.0%, M
o: 0.02-0.4%, sol.Al:0.01-0.1%, Ca: 0.006% or less, B: 0.0005-0.005%, Ti: 0.005-0.05%, and Cu:
0.5% or less, Ni: 0.5% or less, Nb: 0.05% or less, V: include one or more than 0.05% of, P H value represented by it and the following formulas balance iron and unavoidable impurities 1.0 % Or less of the steel is hardened as it is, or after quenching, it is tempered at a low temperature, and a method for producing a high hardness wear-resistant steel with excellent H B ≧ 500, which is excellent in delayed crack resistance after welding.
PH＝Ｃ＋Mn/10＋Mo/6＋Cr/15＋3V＋40P＋100B(%) 本発明において上記式の如くPH≦1.0％に限定した理由
は次のとおりである。即ち、第１図に示す如く、HB＞45
0において、PHが1.0％超では溶接後の遅れ割れが発生
し、1.0％以下ではそれを確実に防止することができる
からである。P H = C + Mn / 10 + Mo / 6 + Cr / 15 + 3V + 40P + 100B (%) The reason for limiting P H ≦ 1.0% as in the above formula in the present invention is as follows. That is, as shown in FIG. 1, H B > 45
At 0, because P H is at 1.0 percent occurs delayed cracking after welding, it is 1.0% or less can prevent it reliably.
また、本発明において化学成分を前記の如く限定した理
由は以下のとおりである。The reason why the chemical components are limited as described above in the present invention is as follows.
Ｃは耐摩耗性の支配因子である硬度を確保するために0.
3％以上は必要であるが、溶接性の点から0.5％以下に限
定した。C is 0. to secure hardness, which is a controlling factor of wear resistance.
3% or more is necessary, but it was limited to 0.5% or less from the viewpoint of weldability.
Siは脱酸上0.05％以上が必要であるが、溶接熱影響部の
靭性確保の点から0.5％以下に限定した。Si needs to be 0.05% or more in terms of deoxidation, but it is limited to 0.5% or less from the viewpoint of ensuring the toughness of the weld heat affected zone.
Mnは母材の靭性及び硬度を確保する上から、0.5％以上
が必要であるが、焼入れ性が低い割にはPH値の係数が大
きいので溶接性の観点から1.5％以下に限定した。Mn from ensuring the toughness and hardness of the base material, it is necessary to more than 0.5%, the low hardenability split was limited to 1.5% or less in terms of so weldability large coefficient of P H value.
ＰはPH値を大きくする有害な元素であるから、コントバ
ランスを考慮した上で出来るだけ低減するのが好まし
く、現行の精練技術をもってすれば、Ｐ≦0.005％とす
ることも可能ではあるが、PH≦1.0％となりうるＰ≦0.0
10％に限定した。Since P is a harmful element which increases the P H value is preferably reduced as much as possible in consideration of the controller balance, if advance the current refining technology, although it is possible to P ≦ 0.005% , P H ≦ 1.0%, P ≦ 0.0
Limited to 10%.
Ｓは靭性の観点から0.005％以下に限定した。S is limited to 0.005% or less from the viewpoint of toughness.
Moは焼入れ性の確保のために0.02％以上添加するもので
あるが、コスト及び溶接性の点から0.4％以下に限定し
た。Mo is added in an amount of 0.02% or more to ensure hardenability, but it is limited to 0.4% or less from the viewpoint of cost and weldability.
Crは安価に焼入れ性を確保できる主要元素であるので、
0.1％以上とし、溶接性の点から1.0％以下に限定した。Since Cr is a main element that can ensure hardenability at low cost,
0.1% or more and limited to 1.0% or less in terms of weldability.
sol.Alは脱酸上0.01％以上必要であり、Ｂを添加する際
には0.04％以上添加することが好ましいが、溶接性の観
点から0.1％以下に限定した。It is necessary to add 0.01% or more of sol.Al for deoxidation, and it is preferable to add 0.04% or more when adding B, but it is limited to 0.1% or less from the viewpoint of weldability.
CaはMnSの圧延による延伸に起因する低温靭性の劣化を
防止するために添加するが、過剰に添加すると却ってCa
系介在物により内質が悪化するため、従来から慣用的に
添加されている0.006％以下とする。Ca is added to prevent the deterioration of the low temperature toughness due to the stretching of MnS due to rolling.
Since the internal quality deteriorates due to system inclusions, it is 0.006% or less, which is conventionally added conventionally.
Ｂは板厚が大きい場合に焼入れ性を向上させて硬度を確
保するために、0.0005％以上0.005％以下の範囲で添加
する。B is added in the range of 0.0005% to 0.005% in order to improve the hardenability and secure the hardness when the plate thickness is large.
Tiはsol.Alと同様にＢ添加時にフリーＮを固定するため
に0.005％以上の添加が必要である。更にTiの添加は、T
iCにより板厚方向の硬度差をなくす効果があるので、板
厚が大きい場合に好ましいが、0.05％を超えて添加する
と溶接部の靭性が劣化するので、上限は0.05％とした。
但しsol.Alを0.04〜0.1％添加する場合にはTiの添加は
省略され得る。Similar to sol.Al, Ti needs to be added in an amount of 0.005% or more to fix free N when B is added. Furthermore, the addition of Ti is T
Since iC has the effect of eliminating the hardness difference in the plate thickness direction, it is preferable when the plate thickness is large, but if added in excess of 0.05%, the toughness of the weld will deteriorate, so the upper limit was made 0.05%.
However, when sol.Al is added by 0.04 to 0.1%, the addition of Ti can be omitted.
更に本発明鋼においては必要に応じてCu,Ni,Nb,Vの１種
または２種以上が下記の範囲において添加されうる。Further, in the steel of the present invention, one or more of Cu, Ni, Nb and V may be added in the following range, if necessary.
Cuは硬度・靭性のバランス上添加することが好ましい
が、Cu割れの観点から0.5％以下に限定した。Although Cu is preferably added in terms of the balance of hardness and toughness, it is limited to 0.5% or less from the viewpoint of Cu cracking.
Niは硬度・靭性のバランス上添加することが好ましい
が、コスト上の観点から0.5％以下に限定した。Ni is preferably added in terms of the balance of hardness and toughness, but it was limited to 0.5% or less from the viewpoint of cost.
Nbは硬度・靭性のバランス上添加することが好ましい
が、継手靭性の観点から0.05％以下に限定した。Although Nb is preferably added in terms of the balance between hardness and toughness, it is limited to 0.05% or less from the viewpoint of joint toughness.
Ｖは硬度・靭性のバランス上添加されうるが、継手靭性
の観点から0.05％以下に限定した。V can be added in the balance of hardness and toughness, but it is limited to 0.05% or less from the viewpoint of joint toughness.
なお、Ｎは本発明において特に限定されるものではない
が、母材の靭性、低温焼戻し、またはガス切断および溶
接時の予熱に際しての青熱脆性の観点から0.005％以下
とするのが有利である。Although N is not particularly limited in the present invention, it is advantageous to set it to 0.005% or less from the viewpoint of the toughness of the base metal, the low temperature tempering, or the blue heat brittleness at the time of preheating during gas cutting and welding. .
本発明における熱処理について説明する。The heat treatment in the present invention will be described.
熱処理は焼入れたままとするか、または焼入れた後低温
焼戻しを行うが、これ等は常法でよい。即ち、焼入れは
850〜1000℃の温度で行い、低温焼戻しは250℃以下の温
度で行うのが常法である。The heat treatment may be carried out by quenching or may be carried out by low temperature tempering after quenching, which may be a conventional method. That is, quenching
The usual method is to carry out at a temperature of 850 to 1000 ° C and to carry out low temperature tempering at a temperature of 250 ° C or less.
近年、直接焼入れを行う省エネルギー制御圧延が発達し
て来ているが、この直接焼入れを行う場合に、直接焼入
れ前の結晶粒を再加熱による焼入れの場合と同等にする
か、またTi、Nb、Ｖ、Ｂ等を添加している場合は、直接
焼入れ前の固溶量を、再加熱による焼入れの場合と同等
にすれば、再加熱焼入れと同等の効果が得られ、むしろ
省合金元素の観点からもその方が好ましい。In recent years, energy-saving controlled rolling that performs direct quenching has been developed, but when performing this direct quenching, the crystal grains before direct quenching are made equivalent to the case of quenching by reheating, or Ti, Nb, When V, B, etc. are added, if the solid solution amount before direct quenching is made equal to that in the case of quenching by reheating, the same effect as reheating and quenching can be obtained, rather, from the viewpoint of alloy saving elements. It is also preferable from the above.
本発明においては前記の如く化学成分範囲を限定するほ
かに、下記式で示されるPH値を1.0％以下とする如く化
学成分量を規制し、しかも焼入れたままとするか、また
は焼入れた後、低温焼戻しを行うことを必須条件とし、
かくしてHB≧500の高硬度を確実に得ると共に溶接後の
遅れ割れを完全に防止するものである。In addition to limiting the chemical component ranges as above in the present invention, the P H value represented by the following formula to regulate the amounts of chemical components as 1.0% or less, yet either remain quenching or quenching after , Making low temperature tempering an essential condition,
Thus, a high hardness of H B ≧ 500 is reliably obtained and delayed cracking after welding is completely prevented.
PH＝Ｃ＋Mn/10＋Mo/6＋Cr/15＋3V＋40P＋100B(%) 第１図は溶接時に侵入した水素による遅れ割れに対する
炭素当量PHを用い、HB≧500の高硬度耐摩耗鋼の溶接後
の遅れ割れの評価結果（○印は遅れ割れなし、●印は遅
れ割れあり）を示すもので、PH:1.0％以下とすることに
よりHB≧500でかつ溶接後の耐遅れ割れ性の優れた高硬
度耐摩耗鋼が得られることが判る。 P H = C + Mn / 10 + Mo / 6 + Cr / 15 + 3V + 40P + 100B (%) Figure 1 uses a carbon equivalent P H for delayed cracking by hydrogen which has entered during welding, after welding of high hardness wear steel H B ≧ 500 delayed cracking of evaluation results (○ mark without delayed cracking, ● mark is delayed cracking) shows a, P H: by 1.0% or less after H B ≧ 500 a and welding resistance to delayed cracking of the excellent high hardness It is understood that wear resistant steel can be obtained.
（実施例） 本発明の実施例を比較例と共に表−１および表−２に示
す。(Examples) Examples of the present invention are shown in Tables 1 and 2 together with comparative examples.
表−１、表−２の結果から、本発明に従えば、HB≧500
でかつ溶接後の耐遅れ割れ性の優れた高硬度耐摩耗鋼が
得られることが明らかである。 From the results of Table-1 and Table-2, according to the present invention, H B ≧ 500
It is clear that a high hardness and wear resistant steel excellent in delayed crack resistance after welding can be obtained.
【図面の簡単な説明】 第１図はPH値とHBが溶接後の遅れ割れに及ぼす影響を示
す図である。BRIEF DESCRIPTION OF THE DRAWINGS FIG. 1 is a diagram showing the influence of P H value and H B on delayed cracking after welding.
───────────────────────────────────────────────────── フロントページの続き (72)発明者 津田 幸夫 愛知県東海市東海町５−３ 新日本製鐵株 式會社名古屋製鐵所内 (72)発明者 間渕 秀里 東京都千代田区大手町２−６―３ 新日本 製鐵株式會社内 (56)参考文献 特開 昭51−2616（ＪＰ，Ａ) 特開 昭55−24966（ＪＰ，Ａ) 特公 昭36−2012（ＪＰ，Ｂ１) ─────────────────────────────────────────────────── ─── Continuation of the front page (72) Inventor Yukio Tsuda 5-3 Tokai-cho, Tokai-shi, Aichi Nippon Steel Co., Ltd. Inside the Nippon Steel Works (72) Inventor Hidesato Mabuchi 2 Otemachi, Chiyoda-ku, Tokyo -6-3 Nippon Steel Co., Ltd. (56) References JP-A-51-2616 (JP, A) JP-A-55-24966 (JP, A) JP-B-36-2012 (JP, B1)
Claims (6)
1.5％、P:0.010％以下、S:0.005％以下、Cr:0.1〜1.0
％、Mo:0.02〜0.4％、sol.Al:0.01〜0.1％、Ca:0.006％
以下を含み、残部鉄および不可避的不純物からなりかつ
下記式で示されるPH値が1.0％以下となる鋼を焼入れた
ままとするか、または焼入れた後、低温焼戻しすること
を特徴とする溶接後の耐遅れ割れ性に優れたHB≧500の
高硬度耐摩耗鋼の製造方法。 PH＝Ｃ＋Mn/10＋Mo/6＋Cr/15＋3V＋40P＋100B(%)1. C: 0.3-0.5%, Si: 0.05-0.5%, Mn: 0.5-
1.5%, P: 0.010% or less, S: 0.005% or less, Cr: 0.1 to 1.0
%, Mo: 0.02-0.4%, sol.Al:0.01-0.1%, Ca: 0.006%
Include the following, or P H value indicated by the result and the following formula the balance iron and unavoidable impurities to remain quenched steel to be 1.0% or less, or quenching after, characterized by low-temperature tempering welding A method for producing a high hardness wear resistant steel with H B ≧ 500 excellent in delayed cracking resistance. P H = C + Mn / 10 + Mo / 6 + Cr / 15 + 3V + 40P + 100B (%)
1.5％、P:0.010％以下、S:0.005％以下、Cr:0.1〜1.0
％、Mo:0.02〜0.4％、sol.Al:0.01〜0.1％、Ca:0.006％
以下、B:0.0005〜0.005％を含み、残部鉄および不可避
的不純物からなりかつ下記式で示されるPH値が1.0％以
下となる鋼を焼入れたままとするか、または焼入れた
後、低温焼戻しすることを特徴とする溶接後の耐遅れ割
れ性に優れたHB≧500の高硬度耐摩耗鋼の製造方法。 PH＝Ｃ＋Mn/10＋Mo/6＋Cr/15＋3V＋40P＋100B(%)2. C: 0.3-0.5%, Si: 0.05-0.5%, Mn: 0.5-
1.5%, P: 0.010% or less, S: 0.005% or less, Cr: 0.1 to 1.0
%, Mo: 0.02-0.4%, sol.Al:0.01-0.1%, Ca: 0.006%
Hereinafter, B: comprises from 0.0005 to 0.005 percent, or P H value indicated by the result and the following formula the balance iron and unavoidable impurities to remain quenched steel to be 1.0% or less, or quenching after low temperature tempering A method for producing a high hardness wear-resistant steel with H B ≧ 500 excellent in delayed cracking resistance after welding, which is characterized by P H = C + Mn / 10 + Mo / 6 + Cr / 15 + 3V + 40P + 100B (%)
1.5％、P:0.010％以下、S:0.005％以下、Cr:0.1〜1.0
％、Mo:0.02〜0.4％、sol.Al:0.01〜0.1％、Ca:0.006％
以下、B:0.0005〜0.005％、Ti:0.005〜0.05％を含み、
残部鉄および不可避的不純物からなりかつ下記式で示さ
れるPH値が1.0％以下となる鋼を焼入れたままとする
か、または焼入れた後、低温焼戻しすることを特徴とす
る溶接後の耐遅れ割れ性に優れたHB≧500の高硬度耐摩
耗鋼の製造方法。 PH＝Ｃ＋Mn/10＋Mo/6＋Cr/15＋3V＋40P＋100B(%)3. C: 0.3-0.5%, Si: 0.05-0.5%, Mn: 0.5-
1.5%, P: 0.010% or less, S: 0.005% or less, Cr: 0.1 to 1.0
%, Mo: 0.02-0.4%, sol.Al:0.01-0.1%, Ca: 0.006%
Below, including B: 0.0005 to 0.005%, Ti: 0.005 to 0.05%,
Or P H value indicated by the result and the following formula the balance iron and unavoidable impurities to remain quenched steel to be 1.0% or less, or after quenching, Re delayed after welding, characterized in that the low-temperature tempering A method for producing high hardness wear-resistant steel with excellent cracking property of H B ≧ 500. P H = C + Mn / 10 + Mo / 6 + Cr / 15 + 3V + 40P + 100B (%)
1.5％、P:0.010％以下、S:0.005％以下、Cr:0.1〜1.0
％、Mo:0.02〜0.4％、sol.Al:0.01〜0.1％、Ca:0.006％
以下、およびCu:0.5％以下、Ni:0.5％以下、Nb:0.05％
以下、V:0.05％以下の１種又は２種以上を含み、残部鉄
および不可避的不純物からなりかつ下記式で示されるPH
値が1.0％以下となる鋼を焼入れたままとするか、また
は焼入れた後、低温焼戻しすることを特徴とする溶接後
の耐低温遅れ性に優れたHB≧500の高硬度耐摩耗鋼の製
造方法。 PH＝Ｃ＋Mn/10＋Mo/6＋Cr/15＋3V＋40P＋100B(%)4. C: 0.3-0.5%, Si: 0.05-0.5%, Mn: 0.5-
1.5%, P: 0.010% or less, S: 0.005% or less, Cr: 0.1 to 1.0
%, Mo: 0.02-0.4%, sol.Al:0.01-0.1%, Ca: 0.006%
Or less, and Cu: 0.5% or less, Ni: 0.5% or less, Nb: 0.05%
Hereinafter, V: P H containing one or two or more of 0.05% or less, balance iron and unavoidable impurities and represented by the following formula
After the value is either remains quenched steel to be 1.0% or less, or quenching, of H B ≧ 500 excellent low-temperature lag of the post-welding, characterized in that the low-temperature tempering of high hardness wear steel Production method. P H = C + Mn / 10 + Mo / 6 + Cr / 15 + 3V + 40P + 100B (%)
1.5％、P:0.010％以下、S:0.005％以下、Cr:0.1〜1.0
％、Mo:0.02〜0.4％、sol.Al:0.01〜0.1％、Ca:0.006％
以下、B:0.0005〜0.005％、およびCu:0.5％以下、Ni:0.
5％以下、Nb:0.05％以下、V:0.05％以下の１種又は２種
以上を含み、残部鉄および不可避的不純物からなりかつ
下記式で示されるPH値が1.0％以下となる鋼を焼入れた
ままとするか、または焼入れた後、低温焼戻しすること
を特徴とする溶接後の耐遅れ割れ性に優れたHB≧500の
高硬度耐摩耗鋼の製造方法。 PH＝Ｃ＋Mn/10＋Mo/6＋Cr/15＋3V＋40P＋100B(%)5. C: 0.3 to 0.5%, Si: 0.05 to 0.5%, Mn: 0.5 to
1.5%, P: 0.010% or less, S: 0.005% or less, Cr: 0.1 to 1.0
%, Mo: 0.02-0.4%, sol.Al:0.01-0.1%, Ca: 0.006%
Below, B: 0.0005 to 0.005%, and Cu: 0.5% or less, Ni: 0.
5%, Nb: 0.05% or less, V: include one or more than 0.05% of the steel P H value indicated by the result and the following formula the balance iron and inevitable impurities is 1.0% or less A method for producing a high hardness wear-resistant steel with H B ≧ 500, which is excellent in delayed crack resistance after welding, characterized by being left as-quenched or quenched and then low-temperature tempered. P H = C + Mn / 10 + Mo / 6 + Cr / 15 + 3V + 40P + 100B (%)
1.5％、P:0.010％以下、S:0.005％以下、Cr:0.1〜1.0
％、Mo:0.02〜0.4％、sol.Al:0.01〜0.1％、Ca:0.006％
以下、B:0.0005〜0.005％、Ti:0.005〜0.05％、およびC
u:0.5％以下、Ni:0.5％以下、Nb:0.05％以下、V:0.05％
以下の１種又は２種以上を含み、残部鉄および不可避的
不純物からなりかつ下記式で示されるPH値が1.0％以下
となる鋼を焼入れたままとするか、または焼入れた後、
低温焼戻しすることを特徴とする溶接後の耐遅れ割れ性
に優れたHB≧500の高硬度耐摩耗鋼の製造方法。 PH＝Ｃ＋Mn/10＋Mo/6＋Cr/15＋3V＋40P＋100B(%)6. C: 0.3 to 0.5%, Si: 0.05 to 0.5%, Mn: 0.5 to
1.5%, P: 0.010% or less, S: 0.005% or less, Cr: 0.1 to 1.0
%, Mo: 0.02-0.4%, sol.Al:0.01-0.1%, Ca: 0.006%
Below, B: 0.0005 to 0.005%, Ti: 0.005 to 0.05%, and C
u: 0.5% or less, Ni: 0.5% or less, Nb: 0.05% or less, V: 0.05%
Comprises one or more of the following, or P H value indicated by the result and the following formula the balance iron and unavoidable impurities to remain quenched steel to be 1.0% or less, or quenching after,
A method for producing a high hardness wear resistant steel with H B ≧ 500 excellent in delayed cracking resistance after welding, characterized by low temperature tempering. P H = C + Mn / 10 + Mo / 6 + Cr / 15 + 3V + 40P + 100B (%)
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP59097461A JPH0686643B2 (en) | 1984-05-17 | 1984-05-17 | Method for producing high hardness wear-resistant steel with HB ≧ 500 excellent in delayed cracking resistance after welding |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP59097461A JPH0686643B2 (en) | 1984-05-17 | 1984-05-17 | Method for producing high hardness wear-resistant steel with HB ≧ 500 excellent in delayed cracking resistance after welding |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS60243250A JPS60243250A (en) | 1985-12-03 |
| JPH0686643B2 true JPH0686643B2 (en) | 1994-11-02 |
Family
ID=14192941
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP59097461A Expired - Lifetime JPH0686643B2 (en) | 1984-05-17 | 1984-05-17 | Method for producing high hardness wear-resistant steel with HB ≧ 500 excellent in delayed cracking resistance after welding |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0686643B2 (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN110565027A (en) * | 2019-09-18 | 2019-12-13 | 舞阳钢铁有限责任公司 | Steel plate with ultrahigh hardness and excellent low-temperature toughness and production method thereof |
Families Citing this family (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH01172550A (en) * | 1987-12-25 | 1989-07-07 | Nippon Steel Corp | Wear-resistant steel excellent in heat check resistance and having high hardness and high toughness |
| KR100445890B1 (en) * | 2002-01-08 | 2004-08-25 | 주식회사 세아베스틸 | A wear resisting steel and a method thereof |
| CN108220811A (en) * | 2018-01-04 | 2018-06-29 | 河南科技大学 | A kind of abrasion-resistant stee and preparation method thereof |
Family Cites Families (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS512616A (en) * | 1974-06-25 | 1976-01-10 | Nippon Steel Corp | CHODAIKAJUYONET SUSHORIREERU |
| JPS5524966A (en) * | 1978-08-10 | 1980-02-22 | Sumitomo Metal Ind Ltd | High tension steel with excellent resistance to sr cracking |
-
1984
- 1984-05-17 JP JP59097461A patent/JPH0686643B2/en not_active Expired - Lifetime
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN110565027A (en) * | 2019-09-18 | 2019-12-13 | 舞阳钢铁有限责任公司 | Steel plate with ultrahigh hardness and excellent low-temperature toughness and production method thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| JPS60243250A (en) | 1985-12-03 |
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