JP4381210B2 - High wear-resistant roll material and high wear-resistant composite roll - Google Patents
High wear-resistant roll material and high wear-resistant composite roll Download PDFInfo
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- 239000000463 material Substances 0.000 title claims description 41
- 239000002131 composite material Substances 0.000 title claims description 9
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 76
- 229910002804 graphite Inorganic materials 0.000 claims description 76
- 239000010439 graphite Substances 0.000 claims description 76
- 229910052758 niobium Inorganic materials 0.000 claims description 19
- 229910052719 titanium Inorganic materials 0.000 claims description 18
- 229910052720 vanadium Inorganic materials 0.000 claims description 15
- 229910052782 aluminium Inorganic materials 0.000 claims description 11
- 229910052710 silicon Inorganic materials 0.000 claims description 10
- 229910052796 boron Inorganic materials 0.000 claims description 8
- 229910052748 manganese Inorganic materials 0.000 claims description 8
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 7
- 229910052750 molybdenum Inorganic materials 0.000 claims description 7
- 229910052804 chromium Inorganic materials 0.000 claims description 6
- 229910052759 nickel Inorganic materials 0.000 claims description 6
- 239000012535 impurity Substances 0.000 claims description 5
- 229910001141 Ductile iron Inorganic materials 0.000 claims description 4
- 150000001247 metal acetylides Chemical class 0.000 claims description 4
- -1 V: Less than 1.0% Substances 0.000 claims description 3
- 229910000831 Steel Inorganic materials 0.000 claims description 3
- 229910052757 nitrogen Inorganic materials 0.000 claims description 3
- 239000010959 steel Substances 0.000 claims description 3
- 229910001208 Crucible steel Inorganic materials 0.000 claims description 2
- 229910001060 Gray iron Inorganic materials 0.000 claims description 2
- 238000005299 abrasion Methods 0.000 claims description 2
- 229910052799 carbon Inorganic materials 0.000 claims description 2
- 229910052742 iron Inorganic materials 0.000 claims description 2
- 230000000694 effects Effects 0.000 description 14
- 239000010410 layer Substances 0.000 description 14
- 238000005266 casting Methods 0.000 description 10
- 238000002425 crystallisation Methods 0.000 description 9
- 230000008025 crystallization Effects 0.000 description 9
- 238000005096 rolling process Methods 0.000 description 9
- 229910045601 alloy Inorganic materials 0.000 description 8
- 239000000956 alloy Substances 0.000 description 8
- 239000000203 mixture Substances 0.000 description 8
- 229910001018 Cast iron Inorganic materials 0.000 description 7
- 238000005087 graphitization Methods 0.000 description 7
- 239000002184 metal Substances 0.000 description 7
- 229910052751 metal Inorganic materials 0.000 description 7
- 239000002245 particle Substances 0.000 description 7
- 238000009750 centrifugal casting Methods 0.000 description 5
- 230000007423 decrease Effects 0.000 description 4
- 229910001567 cementite Inorganic materials 0.000 description 3
- 230000006866 deterioration Effects 0.000 description 3
- 238000010191 image analysis Methods 0.000 description 3
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 description 3
- 239000011159 matrix material Substances 0.000 description 3
- 229910052760 oxygen Inorganic materials 0.000 description 3
- 230000002829 reductive effect Effects 0.000 description 3
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 2
- 230000000052 comparative effect Effects 0.000 description 2
- 239000007789 gas Substances 0.000 description 2
- 238000010438 heat treatment Methods 0.000 description 2
- 238000005098 hot rolling Methods 0.000 description 2
- 230000001050 lubricating effect Effects 0.000 description 2
- 239000001301 oxygen Substances 0.000 description 2
- 230000001376 precipitating effect Effects 0.000 description 2
- 238000001556 precipitation Methods 0.000 description 2
- 239000002994 raw material Substances 0.000 description 2
- 229920006395 saturated elastomer Polymers 0.000 description 2
- 239000007787 solid Substances 0.000 description 2
- 229910004709 CaSi Inorganic materials 0.000 description 1
- 229910001566 austenite Inorganic materials 0.000 description 1
- 230000015556 catabolic process Effects 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 238000006731 degradation reaction Methods 0.000 description 1
- 230000003111 delayed effect Effects 0.000 description 1
- 238000004090 dissolution Methods 0.000 description 1
- 239000012467 final product Substances 0.000 description 1
- 229910052738 indium Inorganic materials 0.000 description 1
- 230000002401 inhibitory effect Effects 0.000 description 1
- 238000011081 inoculation Methods 0.000 description 1
- 230000000670 limiting effect Effects 0.000 description 1
- 238000003754 machining Methods 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 238000000034 method Methods 0.000 description 1
- 150000004767 nitrides Chemical class 0.000 description 1
- 229910052698 phosphorus Inorganic materials 0.000 description 1
- 230000000717 retained effect Effects 0.000 description 1
- 239000002356 single layer Substances 0.000 description 1
- 238000007711 solidification Methods 0.000 description 1
- 230000008023 solidification Effects 0.000 description 1
- 229910052717 sulfur Inorganic materials 0.000 description 1
- 230000009466 transformation Effects 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
- 230000004580 weight loss Effects 0.000 description 1
- 230000002087 whitening effect Effects 0.000 description 1
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Description
本発明は、圧延に用いられるロール材及び該ロール材を用いた複合ロールに関するものであり、より具体的には、低摩擦係数及び高耐摩耗性を有するロール材及び複合ロールに関するものである。 The present invention relates to a roll material used for rolling and a composite roll using the roll material, and more specifically to a roll material and a composite roll having a low friction coefficient and high wear resistance.
熱間圧延用ロールには、耐摩耗性と耐クラック性にすぐれ、熱膨張率の低い材料が望まれている。
その種の材料として、高合金グレン鋳鉄やハイス系材料が使用されている(例えば特許文献１、２参照)。
しかしながら、高合金グレン鋳鉄は、熱膨張率が小さく、耐クラック性にすぐれるが、耐摩耗性が十分ではない問題があった。また、ハイス系材料は、耐摩耗性にはすぐれるが、熱膨張率が大きく、耐クラック性に劣る問題があった。
For a hot rolling roll, a material having excellent wear resistance and crack resistance and a low coefficient of thermal expansion is desired.
As such a material, high-alloy grain cast iron or high-speed material is used (see, for example, Patent Documents 1 and 2).
However, the high alloy grain cast iron has a problem that the thermal expansion coefficient is small and the crack resistance is excellent, but the wear resistance is not sufficient. In addition, the high-speed material has excellent wear resistance, but has a large coefficient of thermal expansion and inferior crack resistance.
これら問題を解決するために、高合金グレン鋳鉄のすぐれた耐クラック性と熱膨張率を具備し、ハイス系材料のすぐれた耐摩耗性を具備する材料の開発が望まれている。 In order to solve these problems, it is desired to develop a material that has excellent crack resistance and thermal expansion coefficient of high alloy glen cast iron and excellent wear resistance of high-speed material.
そこで、特許文献２に示すように、高合金グレン鋳鉄に、ＶやＮｂなどのＭＣ型炭化物形成元素を添加して、耐摩耗性を向上させることが考えられるが、ＭＣ型炭化物生成元素は、白銑化の強い元素であるため、これら元素を添加すると、基地中に晶出する黒鉛の量が少なくなり、脆化してしまう問題があった。また、これら元素から形成されるＭＣ型炭化物によって摩擦係数が高くなると共に、耐クラック性が低下してしまう問題もあった。 Therefore, as shown in Patent Document 2, it can be considered that MC type carbide forming elements such as V and Nb are added to high alloy grain cast iron to improve wear resistance. Since these elements are strong in whitening, there is a problem that when these elements are added, the amount of graphite crystallized in the matrix decreases and becomes brittle. In addition, the MC type carbide formed from these elements has a problem that the friction coefficient increases and crack resistance decreases.
本発明の目的は、耐摩耗性と耐クラック性にすぐれ、熱膨張率の低い熱間圧延用ロールを提供することである。 An object of the present invention is to provide a roll for hot rolling that is excellent in wear resistance and crack resistance and has a low coefficient of thermal expansion.
上記課題を解決するために、本発明の高耐摩耗性ロール材は、重量％にて、Ｃ：３.１〜３.７％、Ｓｉ：０.３〜１.０％、Ｍｎ：０.１〜１.５％、Ｎｉ：２.５〜５.０％、Ｃｒ：１.０〜２.５％、Ｍｏ：０.１〜１.０％、Ａｌ：０.０１〜０.２％、Ｎ：０.００５〜０.０５％、及び、Ｔｉ、Ｎｂ、Ｖから選択される少なくとも１種を合計量で０.２〜２.５％を含み、残部実質的にＦｅであり、
Ｖ：１.０％未満、Ｎｂ：２.５％以下、Ｔｉ：０.５％以下、２.９％≦Ｃ−(０.２４×Ｖ＋０.１３×Ｎｂ＋０.２５×Ｔｉ)＋０.３３×Ｓｉ＋０.５２×Ａｌ＋０.８６×Ｎ≦４.０％を満たす。
In order to solve the above problems, the highly wear-resistant roll material of the present invention is C: 3.1-3.7%, Si: 0.3-1.0%, Mn: 0.3% by weight. 1-1.5%, Ni: 2.5-5.0%, Cr: 1.0-2.5%, Mo: 0.1-1.0%, Al: 0.01-0.2% N: 0.005 to 0.05% and at least one selected from Ti, Nb and V in a total amount of 0.2 to 2.5%, the balance being substantially Fe,
V: Less than 1.0%, Nb: 2.5% or less, Ti: 0.5% or less, 2.9% ≦ C− (0.24 × V + 0.13 × Nb + 0.25 × Ti) + 0.33 × Si + 0.52 × Al + 0.86 × N ≦ 4.0% is satisfied.
また、本発明の高耐摩耗性ロール材は、重量％にて、Ｃ：３.１〜３.７％、Ｓｉ：０.３〜１.０％、Ｍｎ：０.１〜１.５％、Ｎｉ：２.５〜５.０％、Ｃｒ：１.０〜２.５％、Ｍｏ：０.１〜１.０％、Ｂ：０.０１〜０.０５％、Ｎ：０.００５〜０.０５％、Ａｌ：０.０１〜０.２％、及び、Ｔｉ、Ｎｂ、Ｖから選択される少なくとも１種を合計量で０.２〜２.５％を含み、残部実質的にＦｅであり、
Ｖ：１.０未満、Ｎｂ：２.５％以下、Ｔｉ：０.５％以下、２.９％≦Ｃ−(０.２４×Ｖ＋０.１３×Ｎｂ＋０.２５×Ｔｉ)＋０.３３×Ｓｉ＋０.５２×Ａｌ＋１.１×Ｂ＋０.８６×Ｎ≦４.０％を満たす。
Moreover, the high abrasion-resistant roll material of the present invention is C: 3.1-3.7%, Si: 0.3-1.0%, Mn: 0.1-1.5% by weight%. , Ni: 2.5-5.0%, Cr: 1.0-2.5%, Mo: 0.1-1.0%, B: 0.01-0.05%, N: 0.005 -0.05%, Al: 0.01-0.2%, and at least one selected from Ti, Nb, and V in a total amount of 0.2-2.5%, the balance being substantially Fe,
V: Less than 1.0, Nb: 2.5% or less, Ti: 0.5% or less, 2.9% ≦ C− (0.24 × V + 0.13 × Nb + 0.25 × Ti) + 0.33 × Si + 0 It satisfies .52 × Al + 1.1 × B + 0.86 × N ≦ 4.0%.
成分限定理由
Ｃ：３.１〜３.７％
Ｃは主としてＦｅと結合し、セメンタイトを形成すると共に、Ｖ、Ｎｂ、Ｔｉと結合してＭＣ型炭化物を形成する。また、晶出及び析出黒鉛となって摩擦係数を低減する効果がある。しかしながら、含有量が３.１％未満では黒鉛化が促進されず、３.７％を越えると黒鉛が粗大且つ過多となり、耐肌荒れ性及び耐摩耗性の劣化を招く。Ｃの含有量は３.３〜３.５％がさらに望ましい。
Component limitation reason C: 3.1 to 3.7%
C mainly bonds with Fe to form cementite, and also combines with V, Nb, and Ti to form MC type carbide. Moreover, it becomes the crystallization and precipitation graphite and has the effect of reducing a friction coefficient. However, if the content is less than 3.1%, graphitization is not promoted, and if it exceeds 3.7%, the graphite becomes coarse and excessive, leading to deterioration of rough skin resistance and wear resistance. The C content is more preferably 3.3 to 3.5%.
Ｓｉ：０.３〜１.０％
Ｓｉは湯流れ性の確保と黒鉛の晶出、析出のために必要な元素である。しかしながら、０.３％未満ではその効果が十分でなく、１.０％を越えると黒鉛が過多となり黒鉛を起点とする摩耗が激しくなり、耐摩耗性が劣化する。Ｓｉの含有量は０.４〜０.９％がより望ましい。なお、鋳込み時に、０.０５〜０.１５％程度の接種を行ない、最終製品の成分では上記範囲に調整することが望ましい。
Si: 0.3 to 1.0%
Si is an element necessary for ensuring hot water flow and crystallization and precipitation of graphite. However, if the content is less than 0.3%, the effect is not sufficient. If the content exceeds 1.0%, the amount of graphite becomes excessive, and the wear starting from the graphite becomes intense and the wear resistance deteriorates. The Si content is more preferably 0.4 to 0.9%. In addition, at the time of casting, it is desirable to inoculate about 0.05 to 0.15% and adjust the final product components to the above range.
Ｍｎ：０.１〜１.５％
Ｍｎは硬化能を増し、また、原材料中に不可避的に含まれるＳと結合してＭｎ
Ｓを生成し、Ｓによる劣化を防ぐ元素である。Ｓは原材料中に０.１％程度含有されるため、Ｍｎは０.１％以上含有させることが望ましい。しかしながら、１.５％を越えると靭性の低下を招くため好ましくない。Ｍｎの含有量は０.３〜０.９％がより望ましい。
Mn: 0.1 to 1.5%
Mn increases the hardenability and combines with S inevitably contained in the raw material to form Mn.
It is an element that generates S and prevents deterioration due to S. Since S is contained in the raw material by about 0.1%, Mn is preferably contained by 0.1% or more. However, if it exceeds 1.5%, the toughness is lowered, which is not preferable. The content of Mn is more preferably 0.3 to 0.9%.
Ｎｉ：２.５〜５.０％
Ｎｉは基地組織の改良と黒鉛を晶出、析出させる目的で含有させる。２.５％未満であると黒鉛量が過少となりやすく、５.０％を越えるとＳｉの場合と同様に黒鉛が過多となり、また、残留オーステナイトが増加し、後の熱処理によっても強靭組織にすることが難しくなり、耐摩耗性が低下する。Ｎｉの含有量は４.０〜４.９％がより望ましい。
Ni: 2.5-5.0%
Ni is contained for the purpose of improving the base structure and precipitating and precipitating graphite. If the amount is less than 2.5%, the amount of graphite tends to be excessive, and if it exceeds 5.0%, the amount of graphite becomes excessive as in the case of Si, and the retained austenite increases. And the wear resistance is reduced. The Ni content is more preferably 4.0 to 4.9%.
Ｃｒ：１.０〜２.５％
Ｃｒは一部が基地中に固溶して焼入れ性を改善し、耐摩耗性を向上させる。又、セメンタイトにも固溶し、セメンタイトの硬度を向上させる。１.０％未満であれば、このような作用を得ることができず、２.５％を越えると黒鉛化を阻害する。Ｃｒの含有量は１.５〜１.９％がより望ましい。
Cr: 1.0-2.5%
Part of Cr dissolves in the base to improve hardenability and improve wear resistance. It also dissolves in cementite and improves the hardness of cementite. If it is less than 1.0%, such an effect cannot be obtained, and if it exceeds 2.5%, graphitization is inhibited. The Cr content is more preferably 1.5 to 1.9%.
Ｍｏ：０.１〜１.０％
Ｍｏは、主に基地に固溶し、焼入れ性を改善し、耐摩耗性を向上させる。しかしながら、０.１％未満ではこのような効果が不十分であり、１.０％を越えると黒鉛化を阻害する。Ｍｏの含有量は０.３〜０.８％がより望ましい。
Mo: 0.1-1.0%
Mo mainly dissolves in the base to improve hardenability and improve wear resistance. However, if the content is less than 0.1%, such an effect is insufficient. If the content exceeds 1.0%, graphitization is inhibited. The content of Mo is more preferably 0.3 to 0.8%.
Ａｌ：０.０１〜０.２％
ＡｌはＮと結びついて、ＡｌＮを形成し、黒鉛晶出の核となる。黒鉛は、溶湯中に分散しているＡｌＮを基点として晶出する。従って、ＡｌＮの核が基地中に多数分散して存在することにより、晶出する黒鉛も微細に分散する。また、ＡｌＮは溶湯中の酸素とも結合して溶湯中の酸素含有量を低減するため、Ｓｉ接種の効果も大きくなる。さらに、Ａｌは組織の均一性を高める効果もある。含有量が、０.０１％未満であればその効果を十分に得ることができず、０.２％を越えると、このような効果が飽和すると共に、材質を劣化させる。０.０１〜０.１％がより望ましい。
Al: 0.01 to 0.2%
Al combines with N to form AlN, which becomes a nucleus for crystallization of graphite. Graphite is crystallized based on AlN dispersed in the molten metal. Accordingly, the presence of a large number of AlN nuclei dispersed in the matrix causes finely dispersed graphite to be crystallized. Moreover, since AlN combines with oxygen in the molten metal to reduce the oxygen content in the molten metal, the effect of Si inoculation is increased. Further, Al has an effect of improving the uniformity of the structure. If the content is less than 0.01%, the effect cannot be sufficiently obtained. If the content exceeds 0.2%, such an effect is saturated and the material is deteriorated. 0.01 to 0.1% is more desirable.
Ｖ、Ｎｂ、Ｔｉ：少なくとも１種を合計量で０.２〜２.５％、但し、各元素は、Ｖ：１.０％未満、Ｎｂ：２.５％以下、Ｔｉ：０.５％以下とする。
Ｖ、Ｎｂ、ＴｉはＣと結合し、ＭＣ型炭化物を形成し、耐摩耗性を向上させる。しかしながら、合計量が０.２％未満であればその効果が不十分となる。一方、合計量が２.０％を越えるとＭＣ型炭化物が過多となり、摩擦係数が大きくなると共に、黒鉛化を阻害する影響も高くなる。各元素は、Ｖ：０.８％以下、Ｎｂ：０.８％以下、Ｔｉ：０.２％以下がより望ましい。また、Ｖ、Ｎｂ、Ｔｉの含有量は少なくとも１種を合計量で０.４〜２.０％とすることがより望ましい。
なお、Ｖなどの含有により、ロール作製中の割れ(主として鋳造割れ)などが発生しやすくなるが、Ａｌや後述のＢの含有により防止できる。
V, Nb, Ti: 0.2 to 2.5% in total amount of at least one kind, provided that each element is V: less than 1.0%, Nb: 2.5% or less, Ti: 0.5% The following.
V, Nb, and Ti combine with C to form MC-type carbides and improve wear resistance. However, if the total amount is less than 0.2%, the effect is insufficient. On the other hand, if the total amount exceeds 2.0%, MC type carbides become excessive, the friction coefficient increases, and the effect of inhibiting graphitization also increases. Each element is more preferably V: 0.8% or less, Nb: 0.8% or less, and Ti: 0.2% or less. Further, the content of V, Nb, and Ti is more preferably 0.4 to 2.0% as a total amount of at least one kind.
Although inclusion of V or the like tends to cause cracks (mainly casting cracks) during roll production, it can be prevented by inclusion of Al or B described later.
Ｎ：０.００５〜０.０５％
Ｎは合金の溶製上不可避的に混入する元素であるが、Ａｌ又は選択的に含有されるＢと結合して、黒鉛晶出の核となるＡｌＮ又はＢＮを形成する。０.００５％未満ではＡｌ又はＢと結合するのに十分ではないため組織の微細化及び黒鉛化を達成できない。一方、０.０５％を越えると、窒化物を形成し、材質を劣化させる。０.０１〜０.０３％がより望ましい。
N: 0.005-0.05%
N is an element which is inevitably mixed in the melting of the alloy, but is combined with Al or selectively contained B to form AlN or BN serving as a nucleus for crystallization of graphite. If it is less than 0.005%, it is not sufficient for bonding with Al or B, so that the refinement of the structure and graphitization cannot be achieved. On the other hand, if it exceeds 0.05%, a nitride is formed and the material is deteriorated. 0.01 to 0.03% is more desirable.
なお、上記した成分について、Ｖ、Ｎｂ、Ｔｉは、Ｃと１対１で結合するため、Ｃ当量の(０.２４×Ｖ＋０.１３×Ｎｂ＋０.２５×Ｔｉ)が多いほど黒鉛化を阻害する。また、逆にＳｉは黒鉛化を促進し、黒鉛と同じ作用をするＡｌＮは黒鉛量に換算すると０.５２×Ａｌ＋０.８６×Ｎで表せるから、Ｖ、Ｎｂ、Ｔｉ、Ｓｉ及びＡｌについて、２.９％≦Ｃ−(０.２４×Ｖ＋０.１３×Ｎｂ＋０.２５×Ｔｉ)＋０.３３×Ｓｉ＋０.５２×Ａｌ＋０.８６×Ｎ≦４.２％を満たすようにする。３.１≦Ｃ−(０.２４×Ｖ＋０.１３×Ｎｂ＋０.２５×Ｔｉ)＋０.３３×Ｓｉ＋０.５２×Ａｌ＋０.８６×Ｎ≦３.８がより望ましい。 In addition, about the above-mentioned component, since V, Nb, Ti couple | bonds with C on a one-to-one basis, graphitization will be inhibited, so that there is much C equivalent (0.24 * V + 0.13 * Nb + 0.25 * Ti). . On the other hand, Si promotes graphitization, and AlN, which has the same action as graphite, can be expressed as 0.52 × Al + 0.86 × N when converted to the amount of graphite. Therefore, for V, Nb, Ti, Si and Al, 2 0.9% ≦ C− (0.24 × V + 0.13 × Nb + 0.25 × Ti) + 0.33 × Si + 0.52 × Al + 0.86 × N ≦ 4.2%. 3.1 ≦ C− (0.24 × V + 0.13 × Nb + 0.25 × Ti) + 0.33 × Si + 0.52 × Al + 0.86 × N ≦ 3.8 is more desirable.
Ｂ：０.０１〜０.１％
ＢはＮと結びついてＢＮを形成し、黒鉛晶出の核になるため、必要に応じて選択的に含有させる。黒鉛は、前述のＡｌＮと同様に溶湯中に分散しているＢＮを起点として晶出する。従って、ＢＮの核が基地中に多数分散して存在することにより、晶出する黒鉛も微細に分散する。また、ＢＮは、黒鉛と同じ稠密六方構造であるため、固体潤滑作用を有する。さらに、Ｂは組織の均一性を高める効果がある。０.０１％未満であればその効果が十分ではなく、０.１％を越えるとその効果は飽和すると共に、黒鉛量が過多になり、材質の劣化や黒鉛を起点とする肌荒れが起こりやすい。Ｂの含有量は０.０１〜０.０５％がより望ましい。
B: 0.01-0.1%
B is combined with N to form BN and become a nucleus for crystallization of graphite, so that B is selectively contained as necessary. Graphite is crystallized starting from BN dispersed in the molten metal as in the case of AlN described above. Therefore, when many BN nuclei are dispersed in the base, the crystallized graphite is finely dispersed. BN has the same dense hexagonal structure as graphite and therefore has a solid lubricating action. Furthermore, B has an effect of increasing the uniformity of the tissue. If the content is less than 0.01%, the effect is not sufficient. If the content exceeds 0.1%, the effect is saturated, the amount of graphite becomes excessive, and deterioration of the material and rough skin starting from graphite tend to occur. The content of B is more preferably 0.01 to 0.05%.
なお、Ｂを含有する場合、Ｖ、Ｎｂ、Ｔｉ、Ｓｉ、Ａｌ及びＢについて、２.９％≦Ｃ−(０.２４×Ｖ＋０.１３×Ｎｂ＋０.２５×Ｔｉ)＋０.３３×Ｓｉ＋０.５２×Ａｌ＋１.１×Ｂ＋０.８６×Ｎ≦４.０％を満たすようにする。ここで、０.５２×Ａｌ＋１.１×Ｂ＋０.８６×Ｎは、ＡｌＮ及びＢＮの量を黒鉛量に換算したものである。３.１≦Ｃ−(０.２４×Ｖ＋０.１３×Ｎｂ＋０.２５×Ｔｉ)＋０.３３×Ｓｉ＋０.５２×Ａｌ＋１.１×Ｂ＋０.８６×Ｎ≦３.８とすることがより望ましい。 When B is contained, for V, Nb, Ti, Si, Al and B, 2.9% ≦ C− (0.24 × V + 0.13 × Nb + 0.25 × Ti) + 0.33 × Si + 0.52 * Al + 1.1 * B + 0.86 * N ≦ 4.0% is satisfied. Here, 0.52 × Al + 1.1 × B + 0.86 × N is the amount of AlN and BN converted to the amount of graphite. It is more desirable that 3.1 ≦ C− (0.24 × V + 0.13 × Nb + 0.25 × Ti) + 0.33 × Si + 0.52 × Al + 1.1 × B + 0.86 × N ≦ 3.8.
その他、Ｐ、Ｓ、Ｏ等の不可避的な不純物の混入は許容される。しかしながら、これら不純物は材質を脆くするため、合計で約０.２％以下に抑えることが望ましい。 In addition, inevitable impurities such as P, S, and O are mixed. However, since these impurities make the material brittle, it is desirable to keep the total to about 0.2% or less.
本発明の高耐摩耗性ロール材及び高耐摩耗性複合ロールは、上記成分とすることによって、高合金グレン鋳鉄のすぐれた特性を維持しつつ、高耐摩耗化を実現できる、すなわち、黒鉛及びＭＣ型炭化物の晶出量が適度に調整できるから、低摩擦係数、高耐摩耗性、すぐれた耐焼付き性及びすぐれた通板性を実現でき、黒鉛の平均粒面積が上記範囲を満たすことにより、高い耐クラック性を具備できる。
また、基本的な組成が高合金グレン鋳鉄と重複するため、高合金グレン鋳鉄とほぼ同程度のすぐれた熱膨張率を具備する。
The high wear-resistant roll material and the high wear-resistant composite roll of the present invention can achieve high wear resistance while maintaining the excellent characteristics of the high alloy grain cast iron by using the above components, that is, graphite and Since the amount of crystallization of MC type carbide can be adjusted moderately, low friction coefficient, high wear resistance, excellent seizure resistance and excellent plateability can be realized, and the average grain area of graphite satisfies the above range. High crack resistance can be achieved.
Moreover, since the basic composition overlaps with that of the high alloy glen cast iron, it has an excellent thermal expansion coefficient substantially equal to that of the high alloy glen cast iron.
本発明のロール材は、遠心力鋳造や静置鋳造、或いは、特開平０１ー９６３５５公報に示されるような連続肉盛り鋳掛け法により作製することができる。
遠心力鋳造の場合、遠心力鋳造用金型の中に上記組成となるように溶湯を鋳込んで中空状に形成することができる。得られたロール材は、遠心力鋳造金型から取り出して、熱処理、機械加工を施すことによって、単層の圧延用ロールとして用いることができる。
また、必要に応じて、溶湯を鋳込んだ後、次に内層溶湯を鋳込むことにより、外層のロール材と内層が冶金的に一体化された圧延用複合ロールを形成することもできる。
この場合、内層材料として、ねずみ鋳鉄、ダクタイル鋳鉄、黒鉛鋼、又は、２.０％以下のＣを含有する鋳鋼を例示できる。
さらに、外層の鋳造後、内層を鋳込む前に、中間層を鋳込むことにより、外層、中間層、内層が冶金的に一体化した圧延用複合ロールを形成することができる。中間層の成分として、Ｃ：２.５〜４.０％、Ｓｉ：０.５〜３.５％、Ｍｎ：０.２〜１.５％、Ｎｉ：０％を越えて３.０％以下、Ｃｒ：０％を越えて２.５％以下、Ｍｏ：０％を越えて２.０％以下、Ｍｇ：０.０２〜０.１％以下、及び、Ｖ、Ｎｂ、Ｔｉ、Ａｌ、Ｂから選択される少なくとも１種を合計量で０％を超えて２.０％以下を含むダクタイル鋳鉄や、Ｃ：１.０〜２.５％、Ｓｉ：０.５〜１.５％、Ｍｎ：０.２〜１.５％、Ｎｉ：０％を越えて１.５％以下、Ｃｒ：０％を越えて２.５％以下、Ｍｏ：０％を越えて２.０％以下、及び、Ｖ、Ｎｂ、Ｔｉ、Ａｌ及びＢの少なくとも１種を合計量で０％を越えて１.５％以下、及び、残部実質的にＦｅからなる黒鉛を有する材料を例示できる。
The roll material of the present invention can be produced by centrifugal casting, stationary casting, or a continuous overlay casting method as disclosed in JP-A-01-96355.
In the case of centrifugal casting, the molten metal can be cast into a centrifugal casting mold so as to have the above-mentioned composition and formed into a hollow shape. The obtained roll material can be used as a single layer rolling roll by taking it out from a centrifugal casting mold and subjecting it to heat treatment and machining.
Further, if necessary, after casting the molten metal, the inner layer molten metal is then cast to form a composite roll for rolling in which the outer layer roll material and the inner layer are integrated metallurgically.
In this case, examples of the inner layer material include gray cast iron, ductile cast iron, graphite steel, or cast steel containing 2.0% or less of C.
Furthermore, by casting the intermediate layer after casting the outer layer and before casting the inner layer, a composite roll for rolling in which the outer layer, the intermediate layer, and the inner layer are integrated metallurgically can be formed. As components of the intermediate layer, C: 2.5-4.0%, Si: 0.5-3.5%, Mn: 0.2-1.5%, Ni: more than 0% and 3.0% Hereinafter, Cr: more than 0% to 2.5% or less, Mo: more than 0% to 2.0% or less, Mg: 0.02 to 0.1% or less, and V, Nb, Ti, Al, Ductile cast iron containing at least one selected from B in a total amount of more than 0% to 2.0%, C: 1.0 to 2.5%, Si: 0.5 to 1.5%, Mn: 0.2 to 1.5%, Ni: more than 0% to 1.5% or less, Cr: more than 0% to 2.5% or less, Mo: more than 0% to 2.0% or less, In addition, a material having a graphite having a total amount of at least one of V, Nb, Ti, Al, and B exceeding 0% and not more than 1.5%, and the balance substantially consisting of Fe can be exemplified.
得られたロール材(外層)は、黒鉛晶出の核となるＡｌＮ、ＢＮと黒鉛が晶出している。黒鉛、ＡｌＮ及びＢＮは、固体潤滑作用を有しており、圧延時に鋼材との間の摩擦を低減し、圧延荷重を低くすることができるから、圧延時のトラブルを低減できる。また、黒鉛を有しているため、耐焼付き性にもすぐれる。 The obtained roll material (outer layer) crystallizes AlN, BN and graphite, which are the cores of graphite crystallization. Graphite, AlN, and BN have a solid lubricating action, and can reduce friction with the steel during rolling and lower the rolling load, thereby reducing troubles during rolling. Moreover, since it has graphite, it has excellent seizure resistance.
上記組成のロール材(外層)は、任意の面に出現する黒鉛の平均粒面積が４００μm2以下となっていることが望ましい。黒鉛の平均粒面積とは、任意の面に出現した黒鉛粒の数と、その総面積を計測し、得られた総面積を黒鉛粒の数で割ることによって算出することができる。
任意の面のすべてについて、平均粒面積を求めることは困難であるため、該面の任意の領域、例えば、１.９ｍｍ×１.４ｍｍの領域のミクロ組織写真を撮影し、画像解析して、黒色に見える部分の面積及び個数を測定すればよい。このとき、黒色に見える部分は、黒鉛と黒鉛晶出の核となるＡｌＮ及びＢＮである。しかしながら、黒鉛とＡｌＮ、ＢＮとを見分けることは困難であるから、本願では、黒鉛、ＡｌＮ及びＢＮの合計を黒鉛粒としている。
なお、上記において、任意の面とは、ロール材の断面、例えば、縦断面、横断面等や、ロール材の外表面、端面をも含むものとする。
黒鉛の平均粒面積が４００μm2以下となることにより、図１(ａ)に示すように、ロール材の基地(10)中に粗大な黒鉛粒(12)が晶出しているのではなく、図１(ｂ)に示すように、微細な黒鉛粒(14)が多数晶出しているため、ロール材基地(10)にクラック(16)が発生しても、クラック(16)が黒鉛粒(14)に当たることによって、クラックの先端は尖った形ではなく、ほぼ球状となり、クラックの進展を遅らせる(点線で示す)ことができ、耐クラック性を高めることができる。一方、図１(ａ)のように粗大な黒鉛粒(12)の場合、黒鉛粒(12)どうしの間隔が大きいため、クラック(16)が発生したときに、クラック(16)が黒鉛粒(12)に当たらずに延びていくため、耐クラック性に劣る。また、黒鉛面積率が同じ場合、黒鉛の粒度が細かい図１(ｂ)の方が、黒鉛粒子間の距離が短くなり、クラック進展の際にクラックが黒鉛に当たり、進展速度が低下する確率が高くなる。
The roll material (outer layer) having the above composition preferably has an average particle area of graphite appearing on an arbitrary surface of 400 μm 2 or less. The average grain area of graphite can be calculated by measuring the number of graphite grains appearing on an arbitrary surface and the total area and dividing the obtained total area by the number of graphite grains.
Since it is difficult to determine the average grain area for all arbitrary surfaces, a microstructural photograph of an arbitrary region of the surface, for example, a region of 1.9 mm × 1.4 mm, is taken, and image analysis is performed. What is necessary is just to measure the area and number of parts which look black. At this time, the portions that appear black are graphite and AlN and BN serving as nuclei for graphite crystallization. However, since it is difficult to distinguish graphite from AlN and BN, in this application, the total of graphite, AlN, and BN is used as graphite particles.
In addition, in the above, arbitrary surfaces shall include the cross section of a roll material, for example, a longitudinal cross section, a cross section, the outer surface of a roll material, and an end surface.
When the average grain area of graphite is 400 μm 2 or less, coarse graphite grains (12) are not crystallized in the base (10) of the roll material as shown in FIG. As shown in FIG. 1 (b), since a large number of fine graphite grains (14) are crystallized, even if cracks (16) occur in the roll base (10), the cracks (16) become graphite grains (14 ), The tip of the crack is not a pointed shape, but is almost spherical, and the progress of the crack can be delayed (indicated by a dotted line), and the crack resistance can be improved. On the other hand, in the case of coarse graphite particles (12) as shown in FIG. 1 (a), since the interval between the graphite particles (12) is large, when cracks (16) occur, the cracks (16) become graphite particles ( Since it extends without hitting 12), it is inferior in crack resistance. In addition, when the graphite area ratio is the same, the finer the particle size of the graphite, the smaller the distance between the graphite particles, the higher the probability that the crack hits the graphite when the crack progresses and the progress rate decreases. Become.
また、上記組成のロール材(外層)は、ロール材の基地の任意の面に出現する黒鉛の面積率が０.５〜５.０％であり、ＭＣ型炭化物の面積率が１.０％以下であることが望ましい。黒鉛の面積率が０.５％未満であれば、黒鉛晶出による効果を十分に得ることができず、５.０％を越えると、黒鉛を起点とする摩耗が激しくなり、逆に耐摩耗性を劣化させてしまうからである。また、黒鉛は、耐焼付き性を向上するために重要であるが、ＭＣ型炭化物の面積率が１.０％を越えると、基地中に晶出する黒鉛の量が少なくなり、耐焼付き性の劣化と摩擦係数の増大を招来し、通板性が低下してしまう。
黒鉛の面積率及びＭＣ型炭化物の面積率は、上記と同様に、ある面の任意の領域の画像解析により測定することができる。なお、黒鉛の面積率については、黒鉛とＡｌＮ、ＢＮとの見分けは困難であるから、黒鉛、ＡｌＮ及びＢＮの合計を黒鉛の面積率として測定すればよい。
In the roll material (outer layer) having the above composition, the area ratio of graphite appearing on an arbitrary surface of the base of the roll material is 0.5 to 5.0%, and the area ratio of MC type carbide is 1.0%. The following is desirable. If the area ratio of graphite is less than 0.5%, the effect of graphite crystallization cannot be obtained sufficiently, and if it exceeds 5.0%, the wear starting from graphite becomes severe, and conversely the wear resistance. This is because the performance is deteriorated. Graphite is important for improving the seizure resistance. However, if the area ratio of MC type carbide exceeds 1.0%, the amount of graphite crystallized in the matrix decreases, and the seizure resistance is reduced. Degradation and an increase in the coefficient of friction are incurred, and the plate passing property is lowered.
Similarly to the above, the area ratio of graphite and the area ratio of MC type carbide can be measured by image analysis of an arbitrary region on a certain surface. In addition, about the area ratio of graphite, since it is difficult to distinguish between graphite and AlN and BN, the total of graphite, AlN, and BN may be measured as the area ratio of graphite.
さらに、上記組成のロール材は、基地硬さ(マイクロビッカース硬さ：荷重５０ｇｆ)が５５０Ｈｖ以上であることが望ましい。基地硬さが５５０Ｈｖ未満であると、十分な圧延性能を具備できないからである。 Further, the roll material having the above composition desirably has a base hardness (micro Vickers hardness: load 50 gf) of 550 Hv or more. This is because if the base hardness is less than 550 Hv, sufficient rolling performance cannot be provided.
横型遠心力鋳造機を用いて、Ｇno.１２０、鋳込み温度１３１０℃の条件で、直径３００ｍｍ、長さ２００ｍｍ、厚さ５０ｍｍのロール材(発明例１〜７及び比較例１〜７)を作製した。各ロール材の組成を表１に示す。なお、溶解時点でＡｒガス或いはＮ2ガスのバブリングにより、所定のＮ含有量に調整し、鋳込み時には、Ｓｉ：０.１％を目標にＣａＳｉによるＳｉ接種を行なった。凝固後、常温まで冷却した後で、４００℃で２０時間保持する組織調整熱処理を実施した。 Using a horizontal centrifugal casting machine, roll materials (Invention Examples 1-7 and Comparative Examples 1-7) having a diameter of 300 mm, a length of 200 mm, and a thickness of 50 mm were produced under the conditions of Gno. 120 and a casting temperature of 1310 ° C. . Table 1 shows the composition of each roll material. At the time of dissolution, Ar gas or N 2 gas was bubbled to adjust to a predetermined N content, and at the time of casting, Si was inoculated with CaSi with a target of 0.1% Si. After solidification, after cooling to room temperature, a structure adjustment heat treatment was performed by holding at 400 ° C. for 20 hours.
得られたロール材の外側表面から２０ｍｍの位置で直径１０ｍｍ、長さ３５ｍｍのファレックス試験片を採取し、以下の条件で、黒鉛の平均粒面積、黒鉛面積率、ＭＣ型炭化物の面積率、基地硬さ、摩擦係数、及び、摩耗重量を測定した。
黒鉛の平均粒面積、黒鉛面積率及びＭＣ型炭化物の面積率は、試験片の１.９ｍｍ×１.４ｍｍの部分についてミクロ組織写真を撮影し、画像解析を行なうことによって実施した。
基地硬さは、マイクロビッカース硬度計を用いて荷重５０ｇｆの条件で測定した。
摩擦係数及び摩耗重量は、ファレックス試験機を用いて測定した。測定条件は、相手材をＳＳ４００とし、試験荷重を５０ｋｇｆ、保持時間３分で実施した。摩擦係数は、測定された荷重とトルクから算出し、摩耗重量は、試験前後での重量減少量を比較した。
A Falex test piece having a diameter of 10 mm and a length of 35 mm was collected at a position of 20 mm from the outer surface of the obtained roll material. Under the following conditions, the average grain area of graphite, the graphite area ratio, the area ratio of MC type carbide, Base hardness, coefficient of friction, and wear weight were measured.
The average grain area of graphite, the area ratio of graphite, and the area ratio of MC-type carbide were measured by taking a microstructure photograph of a 1.9 mm × 1.4 mm portion of the test piece and performing image analysis.
Base hardness was measured using a micro Vickers hardness tester under a load of 50 gf.
The coefficient of friction and wear weight were measured using a Falex tester. The measurement conditions were such that the counterpart material was SS400, the test load was 50 kgf, and the holding time was 3 minutes. The coefficient of friction was calculated from the measured load and torque, and the wear weight was compared with the weight loss before and after the test.
結果を表２に示す。
表２を参照すると、発明例１〜７は、本発明の組成範囲を満足しているから、黒鉛の平均粒面積、黒鉛の面積率、及び、ＭＣ型炭化物の面積率が好適であり、その結果、基地硬さが高く、摩擦係数が低く、摩耗重量も小さくできたことがわかる。
一方、比較例１〜７は、組成範囲が本発明から外れいるか、黒鉛の平均粒面積、黒鉛の面積率、又は、ＭＣ型炭化物の面積率が本発明の既定値を満足していない。その結果、基地硬さが低くなったり、摩擦係数が高くなったり、摩耗重量が大きくなるなど、圧延用ロールとしての十分な性能を具備できないことがわかる。通板性を安定させるには、摩擦係数は０.３３以下が望ましい。
Referring to Table 2, since Invention Examples 1 to 7 satisfy the composition range of the present invention, the average grain area of graphite, the area ratio of graphite, and the area ratio of MC type carbide are suitable. As a result, it can be seen that the base hardness is high, the friction coefficient is low, and the wear weight can be reduced.
On the other hand, in Comparative Examples 1 to 7, the composition range is out of the present invention, or the average grain area of graphite, the area ratio of graphite, or the area ratio of MC type carbides does not satisfy the predetermined value of the present invention. As a result, it turns out that sufficient performance as a roll for rolling cannot be provided, such as the base hardness being lowered, the friction coefficient being increased, and the wear weight being increased. In order to stabilize the plate passing property, the friction coefficient is desirably 0.33 or less.
上記実施例の説明は、本発明を説明するためのものであって、特許請求の範囲に記載の発明を限定し、或は範囲を減縮する様に解すべきではない。又、本発明の各部構成は上記実施例に限らず、特許請求の範囲に記載の技術的範囲内で種々の変形が可能である。 The above description of the embodiments is for explaining the present invention, and should not be construed as limiting the invention described in the claims or reducing the scope thereof. Moreover, each part structure of this invention is not restricted to the said Example, A various deformation | transformation is possible within the technical scope as described in a claim.
(10) 基地
(12) 黒鉛粒
(14) 黒鉛粒
(16) クラック
(10) Base
(12) Graphite grains
(14) Graphite grains
(16) Crack
Claims (7)
Ｖ：１.０％未満、Ｎｂ：２.５％以下、Ｔｉ：０.５％以下、２.９％≦Ｃ−(０.２４×Ｖ＋０.１３×Ｎｂ＋０.２５×Ｔｉ)＋０.３３×Ｓｉ＋０.５２×Ａｌ＋１.１×Ｂ＋０.８６×Ｎ≦４.０％を満たす高耐摩耗性ロール材。 In weight%, C: 3.1-3.7%, Si: 0.3-1.0%, Mn: 0.1-1.5%, Ni: 2.5-5.0%, Cr : 1.0 to 2.5%, Mo: 0.1 to 1.0%, B: 0.01 to 0.1%, N: 0.005 to 0.05%, Al: 0.01 to 0 0.2% and at least one selected from Ti, Nb, and V in a total amount of 0.2 to 2.5%, the balance being Fe and inevitable impurities ,
V: Less than 1.0%, Nb: 2.5% or less, Ti: 0.5% or less, 2.9% ≦ C− (0.24 × V + 0.13 × Nb + 0.25 × Ti) + 0.33 × High wear-resistant roll material satisfying Si + 0.52 × Al + 1.1 × B + 0.86 × N ≦ 4.0%.
Between the inner layer and the outer layer, C: 1.0 to 2.5%, Si: 0.5 to 1.5%, Mn: 0.2 to 1.5%, Ni: more than 0% and 1. 5% or less, Cr: more than 0% to 2.5% or less, Mo: more than 0% to 2.0% or less, and a total of at least one selected from V, Nb, Ti, Al, B 6. The high wear-resistant composite roll according to claim 5 , further comprising an intermediate layer comprising graphite in an amount of more than 0% and not more than 2.0%, the balance comprising Fe and inevitable impurities .
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| JP5862526B2 (en) * | 2012-09-13 | 2016-02-16 | Ｊｆｅスチール株式会社 | Roll outer layer material for hot rolling and composite roll for hot rolling |
| CN105568127B (en) * | 2015-12-23 | 2018-03-23 | 中钢集团邢台机械轧辊有限公司 | New rail rolling alloy ductile iron rollcogging-roll and its manufacture method |
| CN106636879B (en) * | 2017-02-14 | 2018-04-20 | 广东中天创展球铁有限公司 | A kind of spheroidal graphite roll body of roll and preparation method thereof |
| CN107605465B (en) * | 2017-09-05 | 2020-10-02 | 中石化石油工程技术服务有限公司 | Method for obtaining shale TOC (total organic carbon) parameters during well logging while drilling based on XRF (X-ray fluorescence) elements |
| CN111809116A (en) * | 2020-07-08 | 2020-10-23 | 山东四方工模具材料研究院有限公司 | Multi-element composite reinforced alloy semi-steel sizing/reducing mill roller and preparation method thereof |
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