JP2009030093A - Wear resistant steel sheet excellent in low temperature tempering brittle crack resistance - Google Patents

Wear resistant steel sheet excellent in low temperature tempering brittle crack resistance Download PDF

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JP2009030093A
JP2009030093A JP2007194285A JP2007194285A JP2009030093A JP 2009030093 A JP2009030093 A JP 2009030093A JP 2007194285 A JP2007194285 A JP 2007194285A JP 2007194285 A JP2007194285 A JP 2007194285A JP 2009030093 A JP2009030093 A JP 2009030093A
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resistant steel
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temperature tempering
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JP5145804B2 (en
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Yasuhiro Murota
康宏 室田
Misao Ishikawa
操 石川
Yoshinori Watanabe
好紀 渡邉
Shinji Mitao
眞司 三田尾
Nobuo Shikauchi
伸夫 鹿内
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JFE Steel Corp
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Abstract

<P>PROBLEM TO BE SOLVED: To provide a wear resistant steel sheet excellent in low temperature tempering brittle crack resistance. <P>SOLUTION: The steel sheet has a composition containing specified amounts of C, Si, Mn, Ti, B, Al, P and S, comprising one or more kinds selected from Cu, Ni, Cr, Mo, V and W, and, if required, comprising one or more kinds selected from Ca, REM and Nb, and in which ceq*=C+Mn/6+(Cu+Ni)/15+(Cr+Mo+V)/5+W/10 is ≤0.55% and DI*=33.85×(0.1×C)<SP>0.5</SP>×(0.7×Si+1)×(3.33×Mn+1)×(0.35×Cu+1)×(0.36×Ni+1)×(2.16×Cr+1)×(3×Mo+1)×(1.75×V+1)×(1.5×W+1) is ≥45, and the balance Fe with inevitable impurities, and also has a microstructure where a base phase is composed of martensite with the austenite grain size of ≤30 μm, and whose surface hardness is ≥400HBW10/3000 by Brinell hardness. <P>COPYRIGHT: (C)2009,JPO&INPIT

Description

本発明は、溶接後の熱影響部や、ガス切断、プラズマ切断など熱溶断後の熱影響部で、低温焼戻し脆化温度域に再加熱された領域において発生する割れの防止に優れる耐摩耗鋼に関し、特に産業機械や運搬機器のうち、溶接や溶断などの加工を受けて製造される部材用として好適なものに関する。   The present invention is a heat-resistant steel excellent in preventing cracks generated in a region reheated to a low temperature temper embrittlement temperature range in a heat affected zone after welding or a heat affected zone after thermal fusing such as gas cutting or plasma cutting. In particular, the present invention relates to an industrial machine or a transport device that is suitable for a member manufactured by processing such as welding or fusing.

鋼材の耐摩耗性は、高硬度化することにより向上し、耐摩耗性が要求される部材には、C量を高くし、焼入れ熱処理や焼入れ−低温焼戻し熱処理を実施した耐磨耗鋼板が使用されている。   The wear resistance of steel materials is improved by increasing the hardness, and wear resistant steel plates that have been subjected to quenching heat treatment or quenching-low temperature tempering heat treatment are used for members that require wear resistance. Has been.

しかし、焼入れ熱処理や焼入れ−低温焼戻し熱処理により製造する耐磨耗鋼など高硬度な鋼材は300〜400℃程度の低温焼戻し脆化温度域に再加熱されると、常温に冷却後、遅れ割れが発生する場合がある。溶接や、ガス切断、プラズマ切断など熱溶断で低温焼き戻し脆化温度域に再加熱された部位が存在すると、常温に冷却後、遅れ割れが発生しやすい。   However, when hardened steel materials such as wear-resistant steel produced by quenching heat treatment or quenching-low temperature tempering heat treatment are reheated to a low temperature temper embrittlement temperature range of about 300 to 400 ° C., delayed cracking occurs after cooling to room temperature. May occur. If there is a portion reheated in the low temperature temper embrittlement temperature region by thermal fusing such as welding, gas cutting or plasma cutting, delayed cracking is likely to occur after cooling to room temperature.

耐磨耗鋼を使用する際には、溶接やガス切断などの加工が行われることが多く、ガス切断面近傍や、溶接熱影響部などでは、鋼材が低温焼戻し脆化温度域に再加熱されることを回避することは不可能であり、上述した遅れ割れの発生防止に優れる耐摩耗鋼が要望されている。   When using wear-resistant steel, processing such as welding and gas cutting is often performed, and the steel material is reheated to the low temperature temper embrittlement temperature range in the vicinity of the gas cutting surface and the weld heat affected zone. It is impossible to avoid this, and there is a demand for wear-resistant steel that is excellent in preventing the occurrence of the above-described delayed cracking.

例えば、特許文献1〜6等で提案されている耐遅れ破壊特性に優れる耐摩耗鋼は、製造ままの鋼板で耐遅れ破壊特性を改善するもので、低温焼戻し脆化温度域に再加熱された後の遅れ破壊特性を改善しているわけではない。
特開2002−115024号公報 特開2002−80930号公報 特開平05−51691号公報 特開平01−255622号公報 特開昭63−317623号公報 特開2003−171730号公報
For example, the wear-resistant steel excellent in delayed fracture resistance proposed in Patent Documents 1 to 6 improves the delayed fracture resistance with an as-manufactured steel sheet and was reheated to a low temperature temper embrittlement temperature range. It does not improve later delayed fracture characteristics.
Japanese Patent Application Laid-Open No. 2002-115024 JP 2002-80930 A Japanese Patent Laid-Open No. 05-51691 Japanese Patent Laid-Open No. 01-255622 Japanese Unexamined Patent Publication No. Sho 63-317623 JP 2003-171730 A

そこで、本発明は、溶接や溶断の熱影響により低温焼戻し脆化温度域に加熱された領域における、常温に冷却後の遅れ破壊が抑制された耐低温焼戻し脆化割れ特性に優れる耐磨耗鋼板を提供することを目的とする。   Therefore, the present invention is a wear-resistant steel sheet excellent in low-temperature tempering embrittlement cracking resistance in which delayed fracture after cooling to room temperature is suppressed in a region heated to a low-temperature tempering embrittlement temperature region due to the thermal effect of welding or fusing. The purpose is to provide.

発明者らは、上記目的を達成するために、耐磨耗鋼における耐低温焼戻し脆化割れ特性に影響する各種要因について、鋭意検討し、Cを0.20〜0.35%添加し、Mnを0.45%未満、Pを0.020%以下とすることによって、優れた耐磨耗性を確保しつつ、耐低温焼戻し脆化割れ特性を著しく改善することが可能であることを見出した。   In order to achieve the above-mentioned object, the inventors diligently studied various factors affecting the low-temperature tempering embrittlement cracking property in wear-resistant steel, adding 0.20 to 0.35% of C, Mn It was found that by making the content less than 0.45% and P less than 0.020%, the low temperature tempering embrittlement cracking property can be remarkably improved while ensuring excellent wear resistance. .

耐低温焼戻し脆化割れ特性は、Mass%で、0.23%C−0.25%Si−0.3〜1.5%Mn−0.003〜0.030%P−0.02%Ti−0.0012%Bを含み、Cu、Ni、Cr、Mo,Wを適宜添加し、Ceq*を0.50%と一定とした鋼片を供試鋼とし、25mmtに圧延後、空冷し、その後900℃に再加熱したのちに焼入れし、得られた鋼板について、図1に示すT形すみ肉溶接割れ試験を実施した。溶接方法は、被覆アーク溶接、入熱17kJ/cmとし、3層6パスの溶接を実施した。   The low temperature tempering embrittlement cracking resistance is Mass%, 0.23% C-0.25% Si-0.3-1.5% Mn-0.003-0.030% P-0.02% Ti A steel slab containing −0.0012% B, Cu, Ni, Cr, Mo, W as appropriate, Ceq * constant at 0.50% was used as a test steel, rolled to 25 mmt, air-cooled, Then, after reheating to 900 ° C., quenching was performed, and the obtained steel sheet was subjected to a T-shaped fillet weld cracking test shown in FIG. The welding method was covered arc welding, heat input was 17 kJ / cm, and three-layer six-pass welding was performed.

図2にT形溶接割れ試験結果を、Mn量、P量で整理した結果を示す。Mn量が0.45%以上、または、P量が0.020%を超えると、割れが発生する。   FIG. 2 shows the results of arranging the T-shaped weld crack test results by Mn amount and P amount. When the amount of Mn is 0.45% or more, or when the amount of P exceeds 0.020%, cracking occurs.

本発明は、得られた知見に基づき、さらに検討を加えて完成されたものである。すなわち、本発明の要旨は次のとおりである。
1.質量%で、C:0.20〜0.35%、Si:0.05〜1.0%、Mn:0.45%未満、Ti:0.005〜0.05%、B:0.0003〜0.0030%、Al:0.1%以下、P:0.020%以下、S:0.005%以下を含有し、Cu:0.1〜1.0%、Ni:0.1〜2.0%、Cr:0.1〜1.0%、Mo:0.05〜1.0%、V:0.005〜0.10%、W:0.05〜1.0%の1種または2種以上を含有し、(1)式で示されるCeq*が0.55%以下、(2)式で示されるDI*が45以上で、残部Feおよび不可避的不純物からなる組成を有し、かつ、ミクロ組織がマルテンサイトを基地相とする耐低温焼戻し脆化割れ特性に優れた耐磨耗鋼板。
Ceq*=C+Mn/6+(Cu+Ni)/15+(Cr+Mo+V)/5+W/10・・・・・(1)
DI*=33.85×(0.1×C)0.5 ×(0.7×Si+1)×(3.33×Mn+1)×(0.35×Cu+1)×(0.36×Ni+1)×(2.16×Cr+1)×(3×Mo+1)×(1.75×V+1)×(1.5×W+1)・・・・・(2)
2.1記載の組成に、さらに、Ca:0.0005〜0.0050%、REM:0.0005〜0.0050%の1種または2種を含有し、(1)式で示されるCeq*が0.55%以下、(2)式で示されるDI*が45以上であり、残部Feおよび不可避的不純物からなる組成を有し、かつ、ミクロ組織がマルテンサイトを基地相とする耐低温焼戻し脆化割れ特性に優れた耐磨耗鋼板。
Ceq*=C+Mn/6+(Cu+Ni)/15+(Cr+Mo+V)/5+W/10・・・・・(1)
DI*=33.85×(0.1×C)0.5 ×(0.7×Si+1)×(3.33×Mn+1)×(0.35×Cu+1)×(0.36×Ni+1)×(2.16×Cr+1)×(3×Mo+1)×(1.75×V+1)×(1.5×W+1)・・・・・(2)
3.1または2記載の組成に、更に、Nb:0.005〜0.024%を含有し、(1)式で示されるCeq*が0.55%以下、(2)式で示されるDI*が45以上であり、残部Feおよび不可避的不純物からなる組成を有し、かつ、ミクロ組織が30μm以下の旧オーステナイト粒径であるマルテンサイトを基地相とする耐低温焼戻し脆化割れ特性に優れた耐磨耗鋼板。
Ceq*=C+Mn/6+(Cu+Ni)/15+(Cr+Mo+V)/5+W/10・・・・・(1)
DI*=33.85×(0.1×C)0.5 ×(0.7×Si+1)×(3.33×Mn+1)×(0.35×Cu+1)×(0.36×Ni+1)×(2.16×Cr+1)×(3×Mo+1)×(1.75×V+1)×(1.5×W+1)・・・・・(2)
4.表面硬度がブリネル硬さで400HBW10/3000以上を有する1乃至3のいずれか一つに記載の低温靭性および耐低温脆化焼戻し割れ特性に優れた耐磨耗鋼板。
The present invention has been completed by further investigation based on the obtained knowledge. That is, the gist of the present invention is as follows.
1. In mass%, C: 0.20 to 0.35%, Si: 0.05 to 1.0%, Mn: less than 0.45%, Ti: 0.005 to 0.05%, B: 0.0003 ~ 0.0030%, Al: 0.1% or less, P: 0.020% or less, S: 0.005% or less, Cu: 0.1-1.0%, Ni: 0.1 2.0%, Cr: 0.1-1.0%, Mo: 0.05-1.0%, V: 0.005-0.10%, W: 0.05-1.0% Containing 2 or more species, Ceq * represented by the formula (1) is 0.55% or less, DI * represented by the formula (2) is 45 or more, and has a composition comprising the balance Fe and inevitable impurities. In addition, a wear-resistant steel sheet having excellent low-temperature tempering embrittlement cracking characteristics with a microstructure of martensite as a base phase.
Ceq * = C + Mn / 6 + (Cu + Ni) / 15 + (Cr + Mo + V) / 5 + W / 10 (1)
DI * = 33.85 × (0.1 × C) 0.5 × (0.7 × Si + 1) × (3.33 × Mn + 1) × (0.35 × Cu + 1) × (0.36 × Ni + 1) × (2.16 × Cr + 1) × (3 × Mo + 1) × (1.75 × V + 1) × (1.5 × W + 1) (2)
The composition described in 2.1 further contains one or two of Ca: 0.0005 to 0.0050% and REM: 0.0005 to 0.0050%, and Ceq * represented by the formula (1) 0.55% or less, DI * represented by the formula (2) is 45 or more, has a composition composed of the balance Fe and inevitable impurities, and has a microstructure of martensite as a base phase and low temperature tempering resistance Wear-resistant steel plate with excellent embrittlement cracking properties.
Ceq * = C + Mn / 6 + (Cu + Ni) / 15 + (Cr + Mo + V) / 5 + W / 10 (1)
DI * = 33.85 × (0.1 × C) 0.5 × (0.7 × Si + 1) × (3.33 × Mn + 1) × (0.35 × Cu + 1) × (0.36 × Ni + 1) × (2.16 × Cr + 1) × (3 × Mo + 1) × (1.75 × V + 1) × (1.5 × W + 1) (2)
3.1 or 2 further contains Nb: 0.005 to 0.024%, Ceq * represented by the formula (1) is 0.55% or less, DI represented by the formula (2) * Excellent low-temperature tempering embrittlement cracking resistance with a composition consisting of the balance Fe and unavoidable impurities and martensite with a microstructure of 30 μm or less of the prior austenite grain size. Wear-resistant steel plate.
Ceq * = C + Mn / 6 + (Cu + Ni) / 15 + (Cr + Mo + V) / 5 + W / 10 (1)
DI * = 33.85 × (0.1 × C) 0.5 × (0.7 × Si + 1) × (3.33 × Mn + 1) × (0.35 × Cu + 1) × (0.36 × Ni + 1) × (2.16 × Cr + 1) × (3 × Mo + 1) × (1.75 × V + 1) × (1.5 × W + 1) (2)
4). The wear-resistant steel sheet having excellent low-temperature toughness and low-temperature embrittlement tempering cracking properties according to any one of 1 to 3, having a surface hardness of Brinell hardness of 400 HBW 10/3000 or more.

本発明によれば、溶接やガス切断による熱影響で低温焼戻しを受けた領域における遅れ割れ特性に優れた耐磨耗鋼板を製造することができ、産業上格段の効果を奏する。   ADVANTAGE OF THE INVENTION According to this invention, the wear-resistant steel plate excellent in the delayed cracking characteristic in the area | region which received the low temperature tempering by the heat influence by welding or gas cutting can be manufactured, and there exists a remarkable effect on industry.

まず、本発明の鋼板の組成を規定した理由について説明する。なお、以下の%表示は、いずれも質量%で表す。   First, the reason for defining the composition of the steel sheet of the present invention will be described. In addition, all the following% display is represented by the mass%.

C:0.20〜0.35%
Cは、マトリクス硬度を高硬度化させ耐磨耗性を向上させる元素である。耐磨耗性を著しく改善するためには、0.20%以上の添加が必要である。一方、0.35%を超えて添加すると、溶接性が劣化する。したがって、0.20〜0.35%とした。なお、好ましくは、0.20〜0.30%である。
C: 0.20 to 0.35%
C is an element that increases the matrix hardness and improves the wear resistance. In order to remarkably improve the wear resistance, addition of 0.20% or more is necessary. On the other hand, if added over 0.35%, the weldability deteriorates. Therefore, it was set to 0.20 to 0.35%. In addition, Preferably, it is 0.20 to 0.30%.

Si:0.05〜1.0%
Siは、脱酸元素として有効な元素であり、このような効果を得るためには0.05%以上の含有を必要とする。また、Siは、鋼に固溶して固溶強化により高硬度化に寄与する有効な元素であるが、1.0%を超える含有は、延性、靭性を低下させ、さらに介在物量が増加する。このため、Siは0.05〜1.0%の範囲に限定する。なお、より好ましくは0.05〜0.40%である。
Si: 0.05-1.0%
Si is an effective element as a deoxidizing element, and in order to obtain such an effect, the content of 0.05% or more is required. Si is an effective element that contributes to high hardness by solid solution strengthening by solid solution in steel. However, if the content exceeds 1.0%, ductility and toughness are reduced, and the amount of inclusions is further increased. . For this reason, Si is limited to the range of 0.05 to 1.0%. In addition, More preferably, it is 0.05 to 0.40%.

Mn:0.45%未満
Mnは、Pの粒界偏析を助長し、遅れ破壊を発生しやすくするため、0.45%未満とする。
Mn: less than 0.45% Mn promotes grain boundary segregation of P and makes delayed fracture easy to occur, so it is made less than 0.45%.

一方、焼入れ性確保のためには、一定量を添加することが望ましく、また、合金コスト低減の観点からも、Mn添加は望ましいため、Mn量は0.30%以上とすることが好ましい。   On the other hand, in order to ensure hardenability, it is desirable to add a certain amount, and from the viewpoint of reducing the alloy cost, addition of Mn is desirable, so the amount of Mn is preferably 0.30% or more.

Al:0.1%以下
Alは、脱酸材として添加し、その効果は、0.0020%以上の含有で認められるが、0.1%を超える多量の含有は、鋼の清浄度を低下させる。このため、Alは0.1%以下とする。
Al: 0.1% or less Al is added as a deoxidizer, and the effect is recognized with a content of 0.0020% or more, but a large content exceeding 0.1% lowers the cleanliness of steel. Let For this reason, Al is made 0.1% or less.

Ti:0.005%〜0.05%
Tiは、Nを固定することにより、BN析出を抑制しBの焼入れ性向上効果を助長する効果を有する。その効果を得るためには、0.005%以上の添加が必要である。一方、0.05%を超えて添加すると、TiCを析出し母材靭性を劣化させるため、0.005〜0.05%とする。
Ti: 0.005% to 0.05%
Ti has the effect of suppressing BN precipitation and promoting the effect of improving the hardenability of B by fixing N. In order to obtain the effect, addition of 0.005% or more is necessary. On the other hand, if added over 0.05%, TiC is precipitated and the base metal toughness is deteriorated, so the content is made 0.005 to 0.05%.

B:0.0003%〜0.0030%
Bは、微量添加により、焼入れ性を著しく改善する。その効果を得るためには、0.0003%以上必要である。一方、0.0030%を超えて添加すると溶接性が劣化するため、0.0003%〜0.003%とする。
B: 0.0003% to 0.0030%
B significantly improves the hardenability by adding a small amount. In order to obtain the effect, 0.0003% or more is necessary. On the other hand, if adding over 0.0030%, weldability deteriorates, so the content is made 0.0003% to 0.003%.

P:0.020%以下
Pは、粒界に偏析し、遅れ破壊発生の起点となるため、0.020%以下とする。
P: 0.020% or less P is segregated at the grain boundary and becomes the starting point of delayed fracture occurrence, so is 0.020% or less.

S:0.005%以下
Sは、MnSを形成し、破壊の発生起点となるため、0.005%以下とする。
S: 0.005% or less Since S forms MnS and serves as a starting point of fracture, it is made 0.005% or less.

Cu:0.1〜1.0%、Ni:0.1〜2.0%、Cr:0.1〜1.0%、Mo:0.05〜1.0%、W:0.05〜1.0%、V:0.005〜0.10%のうち、1種または2種以上
Cu:0.1〜1.0%
Cuは、固溶することにより焼入れ性を向上させる元素であり、この効果を得るために0.1%以上の含有を必要とする。一方、1.0%を超える含有は、熱間加工性を低下させる。このため、Cuを添加する場合は、0.1〜1.0%範囲に限定することが好ましい。なお、より好ましくは0.1〜0.5%である。
Cu: 0.1-1.0%, Ni: 0.1-2.0%, Cr: 0.1-1.0%, Mo: 0.05-1.0%, W: 0.05- 1.0%, V: 0.005 to 0.10%, 1 type or 2 types or more Cu: 0.1 to 1.0%
Cu is an element that improves hardenability by solid solution, and needs to contain 0.1% or more in order to obtain this effect. On the other hand, the content exceeding 1.0% decreases the hot workability. For this reason, when adding Cu, it is preferable to limit to 0.1 to 1.0% of range. In addition, More preferably, it is 0.1 to 0.5%.

Ni:0.1〜2.0%
Niは、固溶することにより焼入れ性を向上させる元素であり、このような効果は0.1%以上の含有で顕著となる。一方、2.0%を超える含有は、材料コストを著しく上昇させる。このため、Niを添加する場合は0.1〜2.0%の範囲に限定することが好ましい。なお、より好ましくは0.1〜1.0%である。
Ni: 0.1 to 2.0%
Ni is an element that improves hardenability by solid solution, and such an effect becomes remarkable when the content is 0.1% or more. On the other hand, the content exceeding 2.0% significantly increases the material cost. For this reason, when adding Ni, it is preferable to limit to 0.1 to 2.0% of range. In addition, More preferably, it is 0.1 to 1.0%.

Cr:0.1〜1.0%
Crは、焼入れ性を向上させる効果を有し、このような効果を得るためには、0.1%以上の含有を必要とするが、0.1%を超える含有は、溶接性を低下させる。そのため、Crを添加する場合は0.1〜1.0%の範囲に限定することが好ましい。なお、より好ましくは0.1〜0.80%である。
Cr: 0.1 to 1.0%
Cr has the effect of improving hardenability, and in order to obtain such an effect, the content of 0.1% or more is required, but the content exceeding 0.1% lowers the weldability. . Therefore, when adding Cr, it is preferable to limit to 0.1 to 1.0% of range. In addition, More preferably, it is 0.1 to 0.80%.

Mo:0.05〜1.0%
Moは、焼入れ性を向上させる元素である。このような効果を得るためには、0.05%以上の含有を必要とするが、1.0%を超えて含有すると溶接性を低下させる。そのため、Moを添加する場合は0.05〜1.0%の範囲に限定することが好ましい。なお、より好ましくは、0.05〜0.80%である。
Mo: 0.05-1.0%
Mo is an element that improves hardenability. In order to acquire such an effect, 0.05% or more of content is required, but when it contains exceeding 1.0%, weldability will be reduced. Therefore, when adding Mo, it is preferable to limit to 0.05 to 1.0% of range. In addition, More preferably, it is 0.05 to 0.80%.

W:0.05〜1.0%
Wは、焼入れ性を向上させる元素である。このような効果を得るためには、0.05%以上の含有を必要とするが、1.0%を超えて含有すると溶接性を低下させる。そのため、Wを添加する場合は0.05〜1.0%の範囲に限定することが好ましい。なお、より好ましくは、0.05〜0.80%である。
W: 0.05-1.0%
W is an element that improves hardenability. In order to acquire such an effect, 0.05% or more of content is required, but when it contains exceeding 1.0%, weldability will be reduced. Therefore, when adding W, it is preferable to limit to 0.05 to 1.0% of range. In addition, More preferably, it is 0.05 to 0.80%.

V:0.005〜0.10%
Vは、焼入れ性を向上させる元素である。このような効果を得るためには、0.005%以上必要とするが、0.10%を超えて含有すると溶接性を低下させる。そのため、Vは、0.005〜0.10%の範囲に限定することが好ましい。
V: 0.005-0.10%
V is an element that improves hardenability. In order to obtain such an effect, 0.005% or more is necessary, but if it exceeds 0.10%, the weldability is lowered. Therefore, V is preferably limited to a range of 0.005 to 0.10%.

Ca、REM:0.0005〜0.0050%
CaやREMは、Sと結合し、MnS生成を抑制する。この効果を得るためには、0.0005%以上必要であるが、0.0050%を超えると、鋼の清状度を劣化させる。そのため、CaやREMは、0.0005〜0.0050%とする。
Ca, REM: 0.0005 to 0.0050%
Ca and REM bind to S and suppress MnS generation. In order to obtain this effect, 0.0005% or more is necessary. However, if it exceeds 0.0050%, the cleanliness of the steel is deteriorated. Therefore, Ca and REM are 0.0005 to 0.0050%.

Nb:0.005〜0.024%
Nbは、炭窒化物あるいは炭化物として析出し、組織を微細化し、遅れ破壊発生を抑制する効果を有する。その効果を得るためには、0.005%以上必要である。一方、0.024%を超えて添加すると、粗大な炭窒化物が析出し、破壊の起点となることがあるため、0.005〜0.024%とする。
Nb: 0.005 to 0.024%
Nb precipitates as carbonitrides or carbides, refines the structure, and has the effect of suppressing the occurrence of delayed fracture. In order to obtain the effect, 0.005% or more is necessary. On the other hand, if added over 0.024%, coarse carbonitride precipitates and may be the starting point of fracture, so 0.005 to 0.024%.

Ceq*(=C+Mn/6+(Cu+Ni)/15+(Cr+Mo+V)/5+W/10):0.55%以下
Ceq*が0.55%を超えると、溶接性が劣化する。そのため、0.55%以下とした。
Ceq * (= C + Mn / 6 + (Cu + Ni) / 15 + (Cr + Mo + V) / 5 + W / 10): 0.55% or less When Ceq * exceeds 0.55%, weldability deteriorates. Therefore, it was made into 0.55% or less.

DI*(=33.85×(0.1×C)0.5 ×(0.7×Si+1)×(3.33×Mn+1)×(0.35×Cu+1)×(0.36×Ni+1)×(2.16×Cr+1)×(3×Mo+1)×(1.75×V+1)×(1.5×W+1)):45以上
DI*が45未満の場合、板厚表層からの焼入れ深さが10mmを下回り、耐磨耗鋼としての寿命が短くなる。そのため、DI*は45以上とする。
DI * (= 33.85 × (0.1 × C) 0.5 × (0.7 × Si + 1) × (3.33 × Mn + 1) × (0.35 × Cu + 1) × (0.36 × Ni + 1) × (2.16 × Cr + 1) × (3 × Mo + 1) × (1.75 × V + 1) × (1.5 × W + 1)): 45 or more When DI * is less than 45, the quenching depth from the plate thickness surface layer Is less than 10 mm, and the life as a wear-resistant steel is shortened. Therefore, DI * is 45 or more.

表面硬度がブリネル硬さで400HBW10/3000以上
表面硬度がブリネル硬さで400HBW10/3000未満の場合には、耐摩耗鋼としての寿命が短くなる。そのため、表面硬度をブリネル硬さで400HBW10/3000以上とすることが望ましい。次に、製造方法について説明する。
[製造方法]
本発明に係る耐摩耗鋼板は、上記した組成の溶鋼を、公知の溶製方法で溶製し、連続鋳造法あるいは造塊−分塊圧延法により、所定寸法のスラブ等の鋼素材とすることが好ましい。
When the surface hardness is Brinell hardness of 400 HBW 10/3000 or more, when the surface hardness is Brinell hardness of less than 400 HBW 10/3000, the life of the wear resistant steel is shortened. Therefore, it is desirable that the surface hardness is 400HBW10 / 3000 or more in terms of Brinell hardness. Next, a manufacturing method will be described.
[Production method]
The wear-resistant steel sheet according to the present invention is made by melting the molten steel having the above composition by a known melting method, and using a continuous casting method or an ingot-bundling rolling method as a steel material such as a slab having a predetermined size. Is preferred.

次いで得られた鋼素材を、冷却することなく直後に、または冷却した後に950〜1250℃に再加熱したのち、熱間圧延し、所望の板厚(肉厚)の鋼板とする。熱間圧延直後、あるいは、再加熱して焼入れを行う。必要に応じて300℃以下での焼戻しを実施する。   Subsequently, the obtained steel material is reheated to 950 to 1250 ° C. immediately after cooling or after cooling, and then hot-rolled to obtain a steel plate having a desired plate thickness (wall thickness). Quenching is performed immediately after hot rolling or by reheating. Tempering at 300 ° C. or lower is performed as necessary.

表1に示す組成の溶鋼を、真空溶解炉で溶製し、小型鋼塊(150kg)(鋼素材)とした。これら鋼素材を、1050〜1250℃に加熱したのち、熱間圧延を施して板厚6〜32mmとし、一部の鋼板については、圧延直後に焼入れ(DQ)し、その他の鋼板については、圧延後空冷し、900℃に再加熱後焼入れ(RQ)を行った。   Molten steel having the composition shown in Table 1 was melted in a vacuum melting furnace to obtain a small steel ingot (150 kg) (steel material). These steel materials are heated to 1050 to 1250 ° C. and then hot-rolled to a plate thickness of 6 to 32 mm. Some steel plates are quenched (DQ) immediately after rolling, and other steel plates are rolled. After air cooling, quenching (RQ) was performed after reheating to 900 ° C.

得られた鋼板について、旧オーステナイト粒径測定、表面硬度測定、T形すみ肉溶接割れ試験を下記の要領で実施した。
[旧オーステナイト粒径測定]
得られた鋼板の1/4・t(板厚)部における粒径を測定した。光学顕微鏡で400倍で観察し、100個の旧オーステナイト粒の各々の円相当粒径を測定し、それらの平均値を旧オーステナイト粒径とした。
[表面硬度測定]
JIS規格Z2243(1998)に準拠し、表層下の表面硬度を測定した。測定は、10MMのタングステン硬球を使用し、荷重は3000Kgfとした。
[T形溶接割れ試験]
図1のとおりに実施した。溶接方法は、被覆アーク溶接、入熱17kJ/cmとし、3層6パスの溶接を実施し、試験溶接部長は200mmである。
About the obtained steel plate, the prior austenite particle size measurement, the surface hardness measurement, and the T-shaped fillet weld cracking test were implemented as follows.
[Old austenite particle size measurement]
The particle diameter in the 1/4 * t (plate thickness) part of the obtained steel plate was measured. It observed with 400 times with the optical microscope, the circular equivalent particle diameter of each of 100 old austenite grains was measured, and those average values were made into the prior austenite particle diameter.
[Surface hardness measurement]
In accordance with JIS standard Z2243 (1998), the surface hardness under the surface layer was measured. For the measurement, a 10MM tungsten hard sphere was used, and the load was 3000 kgf.
[T-shaped weld crack test]
It implemented as FIG. The welding method is covered arc welding, heat input is 17 kJ / cm, three-layer six-pass welding is performed, and the test weld length is 200 mm.

得られた結果を表2に示す。本発明例(鋼板No.1,2,3,4、5,6)は、表面硬度が400HBW10/3000以上を有し、かつ、T形隅肉溶接割れ試験で割れが発生していない。   The obtained results are shown in Table 2. The inventive examples (steel plates No. 1, 2, 3, 4, 5, 6) have a surface hardness of 400 HBW 10/3000 or more, and no cracks are generated in the T-shaped fillet weld cracking test.

一方、比較例(鋼板No.7,8)は、T形隅肉溶接割れ試験において、割れが発生している。尚、表2のT形すみ肉溶接割れ試験の表示で「無」は割れの発生が認められなかったもの、「有」は割れの発生が認められたことを示す。   On the other hand, in the comparative example (steel plates No. 7 and 8), cracks occurred in the T-shaped fillet weld cracking test. In the display of the T-shaped fillet weld cracking test in Table 2, “No” indicates that no crack was observed, and “Yes” indicates that crack was observed.

Figure 2009030093
Figure 2009030093

Figure 2009030093
Figure 2009030093

T形隅肉溶接割れ試験を説明する図。The figure explaining a T-shaped fillet weld cracking test. T形隅肉溶接割れ試験結果に及ぼすMn量、P量の影響を示す図。The figure which shows the influence of the amount of Mn and the amount of P which have on the T type fillet weld crack test result.

Claims (4)

質量%で、C:0.20〜0.35%、Si:0.05〜1.0%、Mn:0.45%未満、Ti:0.005〜0.05%、B:0.0003〜0.0030%、Al:0.1%以下、P:0.020%以下、S:0.005%以下を含有し、Cu:0.1〜1.0%、Ni:0.1〜2.0%、Cr:0.1〜1.0%、Mo:0.05〜1.0%、V:0.005〜0.10%、W:0.05〜1.0%の1種または2種以上を含有し、(1)式で示されるCeq*が0.55%以下、(2)式で示されるDI*が45以上で、残部Feおよび不可避的不純物からなる組成を有し、かつ、ミクロ組織がマルテンサイトを基地相とする耐低温焼戻し脆化割れ特性に優れた耐磨耗鋼板。
Ceq*=C+Mn/6+(Cu+Ni)/15+(Cr+Mo+V)/5+W/10・・・・・(1)
DI*=33.85×(0.1×C)0.5 ×(0.7×Si+1)×(3.33×Mn+1)×(0.35×Cu+1)×(0.36×Ni+1)×(2.16×Cr+1)×(3×Mo+1)×(1.75×V+1)×(1.5×W+1)・・・・・(2)
In mass%, C: 0.20 to 0.35%, Si: 0.05 to 1.0%, Mn: less than 0.45%, Ti: 0.005 to 0.05%, B: 0.0003 ~ 0.0030%, Al: 0.1% or less, P: 0.020% or less, S: 0.005% or less, Cu: 0.1-1.0%, Ni: 0.1 2.0%, Cr: 0.1-1.0%, Mo: 0.05-1.0%, V: 0.005-0.10%, W: 0.05-1.0% Containing 2 or more species, Ceq * represented by the formula (1) is 0.55% or less, DI * represented by the formula (2) is 45 or more, and has a composition comprising the balance Fe and inevitable impurities. In addition, a wear-resistant steel sheet having excellent low-temperature tempering embrittlement cracking characteristics with a microstructure of martensite as a base phase.
Ceq * = C + Mn / 6 + (Cu + Ni) / 15 + (Cr + Mo + V) / 5 + W / 10 (1)
DI * = 33.85 × (0.1 × C) 0.5 × (0.7 × Si + 1) × (3.33 × Mn + 1) × (0.35 × Cu + 1) × (0.36 × Ni + 1) × (2.16 × Cr + 1) × (3 × Mo + 1) × (1.75 × V + 1) × (1.5 × W + 1) (2)
請求項1記載の組成に、さらに、Ca:0.0005〜0.0050%、REM:0.0005〜0.0050%の1種または2種を含有し、(1)式で示されるCeq*が0.55%以下、(2)式で示されるDI*が45以上であり、残部Feおよび不可避的不純物からなる組成を有し、かつ、ミクロ組織がマルテンサイトを基地相とする耐低温焼戻し脆化割れ特性に優れた耐磨耗鋼板。
Ceq*=C+Mn/6+(Cu+Ni)/15+(Cr+Mo+V)/5+W/10・・・・・(1)
DI*=33.85×(0.1×C)0.5 ×(0.7×Si+1)×(3.33×Mn+1)×(0.35×Cu+1)×(0.36×Ni+1)×(2.16×Cr+1)×(3×Mo+1)×(1.75×V+1)×(1.5×W+1)・・・・・(2)
The composition according to claim 1, further comprising one or two of Ca: 0.0005 to 0.0050% and REM: 0.0005 to 0.0050%, and Ceq * represented by the formula (1) 0.55% or less, DI * represented by the formula (2) is 45 or more, has a composition composed of the balance Fe and inevitable impurities, and has a microstructure of martensite as a base phase and low temperature tempering resistance Wear-resistant steel plate with excellent embrittlement cracking properties.
Ceq * = C + Mn / 6 + (Cu + Ni) / 15 + (Cr + Mo + V) / 5 + W / 10 (1)
DI * = 33.85 × (0.1 × C) 0.5 × (0.7 × Si + 1) × (3.33 × Mn + 1) × (0.35 × Cu + 1) × (0.36 × Ni + 1) × (2.16 × Cr + 1) × (3 × Mo + 1) × (1.75 × V + 1) × (1.5 × W + 1) (2)
請求項1または2記載の組成に、更に、Nb:0.005〜0.024%を含有し、(1)式で示されるCeq*が0.55%以下、(2)式で示されるDI*が45以上であり、残部Feおよび不可避的不純物からなる組成を有し、かつ、ミクロ組織が30μm以下の旧オーステナイト粒径であるマルテンサイトを基地相とする耐低温焼戻し脆化割れ特性に優れた耐磨耗鋼板。
Ceq*=C+Mn/6+(Cu+Ni)/15+(Cr+Mo+V)/5+W/10・・・・・(1)
DI*=33.85×(0.1×C)0.5 ×(0.7×Si+1)×(3.33×Mn+1)×(0.35×Cu+1)×(0.36×Ni+1)×(2.16×Cr+1)×(3×Mo+1)×(1.75×V+1)×(1.5×W+1)・・・・・(2)
The composition according to claim 1 or 2, further containing Nb: 0.005 to 0.024%, Ceq * represented by the formula (1) is 0.55% or less, and DI represented by the formula (2) * Excellent low-temperature tempering embrittlement cracking resistance with a composition consisting of the balance Fe and unavoidable impurities and martensite with a microstructure of 30 μm or less of the prior austenite grain size. Wear-resistant steel plate.
Ceq * = C + Mn / 6 + (Cu + Ni) / 15 + (Cr + Mo + V) / 5 + W / 10 (1)
DI * = 33.85 × (0.1 × C) 0.5 × (0.7 × Si + 1) × (3.33 × Mn + 1) × (0.35 × Cu + 1) × (0.36 × Ni + 1) × (2.16 × Cr + 1) × (3 × Mo + 1) × (1.75 × V + 1) × (1.5 × W + 1) (2)
表面硬度がブリネル硬さで400HBW10/3000以上を有する請求項1乃至3のいずれか一つに記載の耐低温焼戻し脆化割れ特性に優れた耐磨耗鋼板。   The wear-resistant steel sheet having excellent low-temperature tempering embrittlement cracking resistance according to any one of claims 1 to 3, having a surface hardness of Brinell hardness of 400 HBW 10/3000 or more.
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