JP2009030092A - Wear resistant steel sheet excellent in low temperature toughness and low temperature tempering brittle crack resistance - Google Patents
Wear resistant steel sheet excellent in low temperature toughness and low temperature tempering brittle crack resistance Download PDFInfo
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 54
- 239000010959 steel Substances 0.000 title claims abstract description 54
- 238000005496 tempering Methods 0.000 title claims abstract description 16
- 229910001566 austenite Inorganic materials 0.000 claims abstract description 12
- 239000000203 mixture Substances 0.000 claims abstract description 8
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 7
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 6
- 229910052721 tungsten Inorganic materials 0.000 claims abstract description 6
- 239000012535 impurity Substances 0.000 claims abstract description 5
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 5
- 229910000734 martensite Inorganic materials 0.000 claims abstract description 4
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 4
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 3
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 3
- 238000005336 cracking Methods 0.000 claims description 21
- 238000005299 abrasion Methods 0.000 claims description 2
- 229910052802 copper Inorganic materials 0.000 abstract description 3
- 230000000694 effects Effects 0.000 description 18
- 238000003466 welding Methods 0.000 description 12
- 238000012360 testing method Methods 0.000 description 11
- 230000003111 delayed effect Effects 0.000 description 10
- 238000000034 method Methods 0.000 description 9
- 239000000463 material Substances 0.000 description 8
- 238000001816 cooling Methods 0.000 description 7
- 238000005520 cutting process Methods 0.000 description 7
- 238000010791 quenching Methods 0.000 description 7
- 230000000171 quenching effect Effects 0.000 description 7
- 238000004519 manufacturing process Methods 0.000 description 6
- 238000010438 heat treatment Methods 0.000 description 5
- 239000002245 particle Substances 0.000 description 5
- 229910045601 alloy Inorganic materials 0.000 description 4
- 239000000956 alloy Substances 0.000 description 4
- 238000005098 hot rolling Methods 0.000 description 4
- 239000006104 solid solution Substances 0.000 description 4
- 238000005259 measurement Methods 0.000 description 3
- 238000002844 melting Methods 0.000 description 3
- 230000008018 melting Effects 0.000 description 3
- 238000012545 processing Methods 0.000 description 3
- 238000003303 reheating Methods 0.000 description 3
- 238000005096 rolling process Methods 0.000 description 3
- 230000007704 transition Effects 0.000 description 3
- 230000003749 cleanliness Effects 0.000 description 2
- 230000007423 decrease Effects 0.000 description 2
- 238000007542 hardness measurement Methods 0.000 description 2
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- 239000010410 layer Substances 0.000 description 2
- 239000002244 precipitate Substances 0.000 description 2
- 238000005728 strengthening Methods 0.000 description 2
- 239000002344 surface layer Substances 0.000 description 2
- 244000197975 Solidago virgaurea Species 0.000 description 1
- 235000000914 Solidago virgaurea Nutrition 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- 239000010953 base metal Substances 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 238000009749 continuous casting Methods 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 238000011835 investigation Methods 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 150000001247 metal acetylides Chemical class 0.000 description 1
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Abstract
Description
本発明は、低温靭性および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、低温で使用される部材用として好適なものに関する。 The present invention is low temperature toughness and heat-affected zone after welding, and heat-affected zone after thermal fusing such as gas cutting and plasma cutting, and is excellent in preventing cracks generated in a region reheated to a low temperature temper embrittlement temperature range. The present invention relates to wear-resistant steel, and particularly relates to industrial machines and conveying equipment that are manufactured by being subjected to processing such as welding and fusing, and that are suitable for use at low temperatures.
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 hard steel such as wear-resistant steel manufactured by quenching heat treatment or quenching-low temperature tempering heat treatment is reheated to a low temperature temper embrittlement temperature range of about 300-400 ° 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。 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.
また、耐摩耗鋼は０℃以下の低温域で作業に用いられることも増えており、靭性が低いと、脆性破壊を生じ作業に重大な支障をきたす。一般に鋼の焼入れ硬さはＣ量を増加することで確保できるが、一方で硬度が増すと材質が脆くなって靭性が劣化する。 In addition, wear-resistant steel is increasingly used for work in a low temperature range of 0 ° C. or less, and if the toughness is low, brittle fracture occurs and the work is seriously hindered. Generally, the quenching hardness of steel can be ensured by increasing the amount of C. On the other hand, when the hardness increases, the material becomes brittle and the toughness deteriorates.
このため、低温靭性に優れる耐摩耗鋼が望まれ、例えば、特許文献７、特許文献８、特許文献９などではＣｒやＭｏなどの合金元素を多量に添加することで耐磨耗鋼板の靭性を向上させる技術が開示されている。 For this reason, wear-resistant steel with excellent low-temperature toughness is desired. For example, in Patent Document 7, Patent Document 8, Patent Document 9, and the like, the toughness of a wear-resistant steel sheet can be increased by adding a large amount of alloy elements such as Cr and Mo. Techniques for improving are disclosed.
これらの技術においてＣｒは焼入れ性の向上が目的で、Ｍｏは焼入れ性を向上させると同時に粒界強度を改善する目的で添加されている。また、特許文献７、８では、焼戻し熱処理を実施することにより低温靭性を改善している。 In these techniques, Cr is added for the purpose of improving hardenability, and Mo is added for the purpose of improving hardenability and at the same time improving the grain boundary strength. Moreover, in patent document 7, 8, low temperature toughness is improved by implementing tempering heat processing.
一方、製造プロセスを工夫した技術として特許文献１０に開示されたものがあり、熱間圧延工程でオースフォームを利用することで旧γ粒を展伸させて靭性を改善することが開示されている。
しかしながら特許文献７〜９に記載された耐摩耗鋼は合金元素多量添加により粒界強度を強化して靭性を向上させるもので、合金元素添加コストが高くなる。 However, the wear resistant steels described in Patent Documents 7 to 9 enhance the toughness by strengthening the grain boundary strength by adding a large amount of alloy elements, and the alloy element addition cost becomes high.
特許文献７や特許文献８記載の耐磨耗鋼は、焼戻し熱処理を実施するため硬度が低下し、耐摩耗性への悪影響が避けられない。 The wear-resistant steels described in Patent Document 7 and Patent Document 8 are subjected to tempering heat treatment, so that the hardness decreases, and an adverse effect on wear resistance is inevitable.
また、特許文献１０に記載された耐摩耗鋼の製造方法は、熱間圧延工程でオースフォームを利用するため、熱間圧延は低温仕上げで、製造性が悪く、さらに安定製造のために厳密な温度管理が必要であり、実製造上必ずしも容易なプロセスではない。 Moreover, since the manufacturing method of the wear-resistant steel described in Patent Document 10 uses ausfoam in the hot rolling process, the hot rolling is a low-temperature finish, the manufacturability is poor, and moreover it is strictly for stable production. Temperature control is necessary, and this is not always an easy process in actual production.
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、優れた低温靭性を備えた、すなわち、低温靭性および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 has suppressed low-temperature toughness after cooling to room temperature in a region heated to a low-temperature temper embrittlement temperature region due to the thermal effects of welding and fusing, and has excellent low-temperature toughness, An object is to provide a wear-resistant steel plate having excellent low-temperature tempering embrittlement cracking properties.
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及び低温靭性に影響する各種要因について、鋭意検討し、Ｃを０．２０〜０．３０％添加し、Ｍｎを１．２％以下、Ｐを０．０１０％以下、旧オーステナイト粒径を３０μｍ以下とすることによって、優れた耐磨耗性を確保しつつ、耐低温焼戻し脆化特性を著しく改善することが可能であること、及び結晶粒径を３０μｍ以下にすることによって、低温靭性も改善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 low-temperature tempering embrittlement cracking characteristics and low-temperature toughness in wear-resistant steel, and C was added in an amount of 0.20 to 0.30%. In addition, by making Mn 1.2% or less, P 0.010% or less, and the prior austenite grain size 30 μm or less, the low temperature tempering embrittlement resistance is remarkably improved while ensuring excellent wear resistance. It has been found that low temperature toughness can be improved by making the crystal grain size 30 μm or less.
耐低温焼戻し脆化割れ特性は、Ｍａｓｓ％で、０．２２％Ｃ−０．２５％Ｓｉ−０．４５〜１．５％Ｍｎ−０．００３〜０．０３０％Ｐ−０．１２％Ｍｏ−０．０２％Ｎｂ−０．０１％Ｔｉ−０．００１％Ｂを含み、Ｃｕ、Ｎｉ、Ｃｒ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。 Low-temperature tempering embrittlement cracking resistance is Mass%, 0.22% C-0.25% Si-0.45-1.5% Mn-0.003-0.030% P-0.12% Mo. A steel piece containing -0.02% Nb-0.01% Ti-0.001% B, appropriately adding Cu, Ni, Cr, and having a constant Ceq * of 0.50% was used as a test steel. After rolling to 25 mmt, air cooling, and then reheating to 900 ° C. followed by quenching, the obtained steel sheet was subjected to a T-shaped fillet weld cracking test shown in FIG. The welding method was covered arc welding and 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１．２％を超えるか、または、Ｐ量が０．０１０％を超えると、割れが発生する。これらの鋼板の旧オーステナイト粒径は、全て３０μｍ未満であり、割れの形態は、粒界破面であった。 FIG. 2 shows the results of arranging the T-shaped weld crack test results by Mn amount and P amount. If the Mn content exceeds 1.2% or the P content exceeds 0.010%, cracking occurs. The prior austenite grain sizes of these steel sheets were all less than 30 μm, and the form of cracking was a grain boundary fracture surface.
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：０．２０〜０．３０％、Ｓｉ：０．０５〜１．０％、Ｍｎ：０．４５〜１．２％、Ｎｂ：０．００５〜０．０２４％、Ｔｉ：０．００５〜０．０５％、Ｂ：０．０００３〜０．００３０％、Ａｌ：０．１％以下、Ｐ：０．０１０％以下、Ｓ：０．００５％以下を含有し、Ｍｏ：０．０５〜１．０％、Ｗ：０．０５〜１．０％のいずれか１種以上を含有し、更に、Ｃｕ：０．１〜１．０％、Ｎｉ：０．１〜２．０％、Ｃｒ：０．１〜１．０％、Ｖ：０．００５〜０．１０％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、ミクロ組織が旧オーステナイト粒径が３０μｍ以下のマルテンサイトを基地相とする低温靭性および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、ミクロ組織が旧オーステナイト粒径が３０μｍ以下のマルテンサイトを基地相とする低温靭性および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．表面硬度がブリネル硬さで４００ＨＢＷ１０／３０００以上有する１または２に記載の低温靭性および耐低温脆化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 0.30%, Si: 0.05 to 1.0%, Mn: 0.45 to 1.2%, Nb: 0.005 to 0.024%, Ti: 0.005 to 0.05%, B: 0.0003 to 0.0030%, Al: 0.1% or less, P: 0.010% or less, S: 0.005% or less, Mo: 0 0.05-1.0%, W: Any one or more of 0.05-1.0%, Cu: 0.1-1.0%, Ni: 0.1-2.0 %, Cr: 0.1 to 1.0%, V: 0.005 to 0.10%, or a Ceq * represented by the formula (1) is 0.55% or less, (2) A martensite having a DI * of 45 or more, a balance Fe and inevitable impurities, and a microstructure having a prior austenite grain size of 30 μm or less. Abrasion steel sheet excellent in low temperature toughness and low temperature tempering embrittlement cracking properties to goldenrod.
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) Is 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 with a prior austenite grain size of 30 μm or less. A wear-resistant steel sheet with excellent low-temperature toughness and low-temperature tempering embrittlement cracking characteristics.
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. 3. A wear-resistant steel sheet having excellent low-temperature toughness and low-temperature embrittlement cracking properties according to 1 or 2 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、且つ低温靭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。 According to the present invention, it is possible to produce a wear-resistant steel sheet having excellent delayed cracking characteristics in a region subjected to low-temperature tempering due to heat influence by welding or gas cutting, and excellent in low-temperature toughness. Play.
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：０．２０〜０．３０％
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、０．３０％を超えて添加すると、溶接性が劣化する。したがって、０．２０〜０．３０％とした。なお、好ましくは、０．２０〜０．２８％である。
C: 0.20 to 0.30%
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 0.30%, weldability deteriorates. Therefore, it was set to 0.20 to 0.30%. In addition, Preferably, it is 0.20 to 0.28%.
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：０．４５〜１．２％
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。マルテンサイトの旧オーステナイト粒径が３０μｍ以下の場合、Ｍｎ量を１．２％以下とすることで、粒界破壊の発生が抑制される。
Mn: 0.45 to 1.2%
Mn promotes the grain boundary segregation of P and makes delayed fracture easier to occur. When the prior austenite grain size of martensite is 30 μm or less, the occurrence of grain boundary fracture is suppressed by setting the Mn content to 1.2% or less.
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添加は望ましく、Ｍｎ量は０．４５％〜１．２％の範囲に限定する。 On the other hand, in order to ensure hardenability, it is desirable to add a certain amount, and also from the viewpoint of alloy cost reduction, addition of Mn is desirable, and the amount of Mn is limited to a range of 0.45% to 1.2%. To do.
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.
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 carbonitrides precipitate and may become the starting point of fracture, so the content is made 0.005% to 0.024%.
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。より好ましくは、０．０００５〜０．００２０％である。
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%. More preferably, it is 0.0005 to 0.0020%.
Ｐ：０．０１０％以下
Ｐは、粒界に偏析し、遅れ破壊発生の起点となるため、０．０１０％以下とする。
P: 0.010% or less P is segregated at the grain boundary and becomes the starting point of delayed fracture occurrence, so is 0.010% 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.
Ｍｏ：０．０５〜１．０％、Ｗ：０．０５〜１．０％のいずれか１種以上
Ｍｏ：０．０５〜１．０％
Ｍｏは、焼入れ性を向上させるためにとくに有効な元素である。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。
Any one or more of Mo: 0.05 to 1.0%, W: 0.05 to 1.0% Mo: 0.05 to 1.0%
Mo is an element particularly effective for improving the 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ために特に有効な元素である。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。Ｍｏ，Ｗはいずれか１種以上の含有を必須とする。
W: 0.05-1.0%
W is an element particularly effective for improving 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%. Mo and W must contain at least one of them.
Ｃｕ：０．１〜１．０％、Ｎｉ：０．１〜２．０％、Ｃｒ：０．１〜１．０％、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 to 1.0%, Ni: 0.1 to 2.0%, Cr: 0.1 to 1.0%, V: 0.005 to 0.10%, 1 type or 2 More than seed Cu: 0.1-1.0%
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%.
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%.
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 thickness of 6 to 32 mm. Some steel plates are quenched immediately after rolling (DQ), 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、シャルピ−衝撃試験、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。
［シャルピー衝撃試験］
ＪＩＳ規格Ｚ２２４２に準拠し、破面遷移温度を測定した。得られた結果を表２に示す。
本発明例（鋼板Ｎｏ．１，２，３，４）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せず、また、破面遷移温度が０℃以下の優れた低温靭性を有している。
The obtained steel sheet was subjected to prior austenite particle size measurement, surface hardness measurement, Charpy impact test, and T-shaped fillet weld cracking test in the following manner.
[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.
[Charpy impact test]
The fracture surface transition temperature was measured according to JIS standard Z2242. The obtained results are shown in Table 2.
The inventive examples (steel plates No. 1, 2, 3, 4) have a surface hardness of 400 HBW 10/3000 or more, are not cracked in the T-type fillet weld cracking test, and have a fracture surface transition temperature. Has excellent low temperature toughness of 0 ° C. or less.
一方、比較例（鋼板Ｎｏ．５，６，７）は、Ｔ形隅肉溶接割れ試験において、割れが発生し、および／または破面遷移温度が０℃以上と本発明例に対して靭性に劣る。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. 5, 6, 7), in the T-shaped fillet weld cracking test, cracks occurred and / or the fracture surface transition temperature is 0 ° C. or higher, which is tougher than the inventive example. Inferior. 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.
Claims (3)
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 0.30%, Si: 0.05 to 1.0%, Mn: 0.45 to 1.2%, Nb: 0.005 to 0.024%, Ti: 0.005 to 0.05%, B: 0.0003 to 0.0030%, Al: 0.1% or less, P: 0.010% or less, S: 0.005% or less, Mo: 0 0.05 to 1.0%, W: 0.05 to 1.0%, or one or more of Cu: 0.1 to 1.0%, Ni: 0.1 to 2. 1% or more of 0%, Cr: 0.1 to 1.0%, V: 0.005 to 0.10%, and Ceq * represented by the formula (1) is 0.55% or less , (2) is a martensite having a DI * of 45 or more, the balance Fe and inevitable impurities, and a microstructure with a prior austenite grain size of 30 μm or less Abrasion steel sheet excellent in low temperature toughness and low temperature tempering embrittlement cracking characteristics to the 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)
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) Is 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 with a prior austenite grain size of 30 μm or less. A wear-resistant steel sheet with excellent low-temperature toughness and low-temperature tempering embrittlement cracking characteristics.
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)
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