JP4937634B2 - Crushing blade steel and crushing blade manufacturing method - Google Patents
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- JP4937634B2 JP4937634B2 JP2006128900A JP2006128900A JP4937634B2 JP 4937634 B2 JP4937634 B2 JP 4937634B2 JP 2006128900 A JP2006128900 A JP 2006128900A JP 2006128900 A JP2006128900 A JP 2006128900A JP 4937634 B2 JP4937634 B2 JP 4937634B2
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- 229910000831 Steel Inorganic materials 0.000 title claims description 20
- 239000010959 steel Substances 0.000 title claims description 19
- 238000004519 manufacturing process Methods 0.000 title claims description 6
- 238000005496 tempering Methods 0.000 claims description 15
- 229910001566 austenite Inorganic materials 0.000 claims description 13
- 230000008859 change Effects 0.000 claims description 12
- 238000010791 quenching Methods 0.000 claims description 10
- 230000000171 quenching effect Effects 0.000 claims description 10
- 230000000717 retained effect Effects 0.000 claims description 10
- 230000032683 aging Effects 0.000 claims description 6
- 238000005520 cutting process Methods 0.000 claims description 6
- 229910052720 vanadium Inorganic materials 0.000 claims description 5
- 229910001315 Tool steel Inorganic materials 0.000 claims description 4
- 229910052750 molybdenum Inorganic materials 0.000 claims description 4
- 229910052758 niobium Inorganic materials 0.000 claims description 4
- 229910052721 tungsten Inorganic materials 0.000 claims description 4
- 239000012535 impurity Substances 0.000 claims description 2
- 229910052742 iron Inorganic materials 0.000 claims description 2
- 239000000463 material Substances 0.000 description 10
- 230000000052 comparative effect Effects 0.000 description 9
- 239000002699 waste material Substances 0.000 description 9
- 238000005336 cracking Methods 0.000 description 6
- 150000001247 metal acetylides Chemical class 0.000 description 5
- 238000000034 method Methods 0.000 description 5
- 229910052804 chromium Inorganic materials 0.000 description 4
- 238000005299 abrasion Methods 0.000 description 3
- 229910052799 carbon Inorganic materials 0.000 description 3
- 238000001816 cooling Methods 0.000 description 3
- 238000010438 heat treatment Methods 0.000 description 3
- 238000005259 measurement Methods 0.000 description 3
- 239000000203 mixture Substances 0.000 description 3
- 230000008569 process Effects 0.000 description 3
- 230000035882 stress Effects 0.000 description 3
- 229910000851 Alloy steel Inorganic materials 0.000 description 2
- 238000005255 carburizing Methods 0.000 description 2
- 238000011109 contamination Methods 0.000 description 2
- 238000000354 decomposition reaction Methods 0.000 description 2
- 230000007423 decrease Effects 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 238000005516 engineering process Methods 0.000 description 2
- 230000007613 environmental effect Effects 0.000 description 2
- 229910052748 manganese Inorganic materials 0.000 description 2
- 238000001556 precipitation Methods 0.000 description 2
- 238000004064 recycling Methods 0.000 description 2
- 230000001105 regulatory effect Effects 0.000 description 2
- 238000005096 rolling process Methods 0.000 description 2
- 229910052710 silicon Inorganic materials 0.000 description 2
- 239000002436 steel type Substances 0.000 description 2
- 238000003466 welding Methods 0.000 description 2
- 229910000746 Structural steel Inorganic materials 0.000 description 1
- 238000002441 X-ray diffraction Methods 0.000 description 1
- 238000005054 agglomeration Methods 0.000 description 1
- 230000002776 aggregation Effects 0.000 description 1
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- 238000000137 annealing Methods 0.000 description 1
- 230000033228 biological regulation Effects 0.000 description 1
- 229910001567 cementite Inorganic materials 0.000 description 1
- 239000006185 dispersion Substances 0.000 description 1
- 239000004615 ingredient Substances 0.000 description 1
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 description 1
- 238000003754 machining Methods 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 238000005457 optimization Methods 0.000 description 1
- 238000005498 polishing Methods 0.000 description 1
- 230000002028 premature Effects 0.000 description 1
- 230000009467 reduction Effects 0.000 description 1
- 238000003892 spreading Methods 0.000 description 1
- 230000007480 spreading Effects 0.000 description 1
- 238000009628 steelmaking Methods 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
Classifications
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/20—Recycling
Description
本発明は、高靱性と高耐摩耗性および経年変化特性を要求される廃棄物破砕機の破砕刃用鋼およびそれを使用した破砕刃の製造方法に関するものである。 The present invention relates to a steel for a crushing blade of a waste crusher that requires high toughness, high wear resistance, and aging characteristics, and a crushing blade manufacturing method using the same.
従来、各種用途の刃物材料として、特殊鋼第４８巻第１１号第４７〜４８頁（非特許文献１）や、リサイクルカッタ用鋼について、型技術第１１巻第８号第１頁（非特許文献２）に開示されている。また、山陽特殊製鋼技報Ｖｏｌ．１２、Ｎｏ．１．第６９頁（非特許文献３）には、資源の有効利用・環境保護に貢献する破砕刃用材料が開示されている。上記非特許文献では、廃棄物破砕刃への適用例として、冷間ダイス鋼ＪＩＳ ＳＫＤ１１、熱間ダイス鋼ＪＩＳ ＳＫＤ６１、高速度工具鋼ＪＩＳ ＳＫＨ５１や各社開発鋼など破棄物の種類や使用目的によって、選定鋼種が多岐に渡って紹介されており、硬さや衝撃特性に関して述べられている。しかしながら、いずれも経年変化に着目した記述は全くない。 Conventionally, as a blade material for various uses, special steel Vol. 48, No. 11, pp. 47-48 (Non-patent Document 1), and steel for recycling cutter, die technology Vol. 11, No. 8, page 1 (Non-patent) Document 2). In addition, Sanyo Special Steel Engineering Report Vol. 12, no. 1. On page 69 (Non-Patent Document 3), a crushing blade material that contributes to effective use of resources and environmental protection is disclosed. In the above non-patent literature, as examples of application to waste crushing blades, depending on the type and purpose of use of the waste such as cold die steel JIS SKD11, hot die steel JIS SKD61, high speed tool steel JIS SKH51 and steel developed by each company, A wide range of selected steel types are introduced, and the hardness and impact properties are described. However, there is no description focusing on aging.
一方、特開２００５−２４４７号公報（特許文献１）「浸炭用材料と破砕機用刃体の製造方法」には、浸炭処理およびサブゼロ処理を実施することで硬さと靱性を有する刃体の製造方法が開示されているが、浸炭による硬化層は０．５〜１．５ｍｍ程度であり、耐摩耗性は不十分である上、表面部のみ硬化しても内部が軟らかい場合、硬化層の剥離による欠けが発生し、長寿命は期待できない。 On the other hand, Japanese Patent Laid-Open No. 2005-2447 (Patent Document 1) “Manufacturing Method of Carburizing Material and Crusher Blade” manufactures a blade having hardness and toughness by performing a carburizing process and a sub-zero process. Although the method is disclosed, the hardened layer by carburization is about 0.5 to 1.5 mm, the abrasion resistance is insufficient, and the hardened layer is peeled off when the inside is soft even if only the surface portion is hardened. Due to the chipping, long life cannot be expected.
また、特開平１１−５７５１７号公報（特許文献２）「破砕用の回転刃」には、合金鋼で作製した回転刃に穿設した取付け穴で耐摩耗性に優れた超硬質工具材料を装着することで、廃棄物の異物混入による刃具の欠損に対する安定性とメンテナンス性が改善しているが、取付け穴の加工費用や超硬質工具材料が大幅なコストアップとなる。 In addition, in JP-A-11-57517 (Patent Document 2) “Crushing rotary blade”, a super hard tool material with excellent wear resistance is mounted by a mounting hole drilled in a rotary blade made of alloy steel. This improves the stability and maintainability of the cutting tool due to foreign matter contamination of the waste, but increases the machining cost of the mounting holes and the super hard tool material.
また、特開平１１−１６５０９０号公報（特許文献３）「切断破砕用カッターの表面硬層材および切断破砕用カッター」には、構造用鋼、工具鋼で作製した円盤型カッター刃先に、より硬質な表面硬層材を肉盛溶着して耐摩耗性を向上しているが、肉盛と研磨によるコストアップ、肉盛層は靱性が低く割れ、欠けが発生するなどの問題がある。さらに、特開２００５−３１９５４５号公報（特許文献４）には、低合金鋼で作製した刃本体の刃先部０．５〜７ｍｍに６０ＨＲＣ以上の溶接材料を肉盛溶接し、耐摩耗性を向上させているが、上記同様に、靱性が低く割れ、欠けが発生するなどの問題がある。
一方、近年の地球環境問題への関心の高まりから、廃棄物の分別回収やリサイクル活動が急速に広まっている。これら資源有効活用への取り組みにおいて、破砕機は廃棄物を再利用するための、破砕・選別工程で重要な役割を果している。また、廃棄物処理量の増加への対応、埋め立て地や焼却炉の延命化への対応から、破砕機による廃棄物の減容化への取り組みが重要となっている。 On the other hand, due to the recent growing interest in global environmental issues, waste collection and recycling activities are rapidly spreading. In efforts to effectively use these resources, crushers play an important role in crushing and sorting processes to reuse waste. In addition, efforts to reduce the volume of waste using a crusher are important in order to respond to the increase in the amount of waste treatment and to extend the life of landfills and incinerators.
従来、このような多種多様な用途で用いられる破砕機の破砕刃には、ＳＣやＳＣＭ系などの材料が用いられていたが、最近の長寿命へのニーズの高まりから耐摩耗性に優れるＳＫＤ（ダイス鋼）やＳＫＨ（ハイス）が汎用材として使用されるようになってきた。 Conventionally, materials such as SC and SCM have been used for the crushing blades of crushers used in such a wide variety of applications, but SKD has excellent wear resistance due to the recent increasing demand for long life. (Die steel) and SKH (high speed) have come to be used as general-purpose materials.
しかし、ＳＫＤやＳＫＨは焼入れ焼戻しにより高硬度が得られるが、ＳＣＭなどに比べると靱性が低下するため、異物混入が避けられない都市ゴミなどの破砕機においては、異物噛込みにより１枚の破砕刃が大割れして、それが周囲にも影響を及ぼし重大な設備トラブルを招くケースが増加している。 However, SKD and SKH can be hardened by quenching and tempering. However, since the toughness is lower than SCM, etc., in a crusher such as municipal waste that cannot avoid contamination, one piece is broken by biting of foreign matter. Increasingly, the blade is cracked, which affects the surroundings and causes serious equipment troubles.
上述したような問題を解消するために、発明者らは鋭意開発を進めた結果、破砕機刃物の割れ・欠けの原因となっている靱性と長寿命を実現する耐摩耗性を兼備するために基本成分を見直した。また、早期割れ・欠け原因について多くのケースで調査、検討した結果、使用開始後の経年変化を抑制するための基本成分の見直しと熱処理の実施によって、早期割れ・欠けを回避したものである。 In order to solve the problems as described above, the inventors have intensively developed, in order to combine the toughness that causes cracking and chipping of the crusher blade and the wear resistance that realizes a long life. The basic ingredients were reviewed. In addition, as a result of investigating and examining the cause of early cracking and chipping in many cases, the early cracking and chipping were avoided by reviewing the basic components to suppress the secular change after the start of use and conducting heat treatment.
上記解決手段として、靱性改善のために主にＳｉ量の低減などの化学成分の最適化を行う。また、経年変化対策として、Ｃｒ量を増加させて焼入れ時の残留オーステナイトを減少させると共に、焼戻しを５５０〜６００℃の高温で２回以上実施して残留オーステナイト量を１．０％以下とすることで、使用開始後の残留オーステナイトの分解による膨張を伴う経年変化を回避することが可能となった。 As a solution to the above problem, optimization of chemical components such as reduction of the amount of Si is mainly performed to improve toughness. In addition, as a countermeasure against secular change, the amount of Cr is increased to reduce the retained austenite at the time of quenching, and tempering is performed at a high temperature of 550 to 600 ° C. at least twice to reduce the amount of retained austenite to 1.0% or less. Thus, it has become possible to avoid the secular change accompanied by the expansion due to the decomposition of the retained austenite after the start of use.
その発明の要旨とするところは、
（１）質量％で、Ｃ：０．３〜０．５％、Ｓｉ：０．２〜０．５％、Ｍｎ：０．１〜１．０％、Ｃｒ：４．０〜６．０％、ＭｏおよびＷの内の１種または２種をＭｏ＋１／２Ｗ：０．８〜２．５％、ＶおよびＮｂの内の１種または２種をＶ＋１／２Ｎｂ：０．３〜１．０％、を含有し、残部をＦｅと不可避的不純物からなることを特徴とする耐摩耗性に優れ、かつ経年変化を抑制した破砕用刃物用鋼。
（２）前記（１）に記載の鋼を使用して、刃物形状に切削加工し、焼入れ後、５５０〜６００℃の高温焼戻しを２回以上行うことにより残留オーステナイト量を１．０％以下としたことを特徴とする経年変化を抑制した破砕刃の製造方法にある。
The gist of the invention is that
(1) By mass%, C: 0.3 to 0.5%, Si: 0.2 to 0.5%, Mn: 0.1 to 1.0%, Cr: 4.0 to 6.0% One or two of Mo and W are Mo + 1 / 2W: 0.8 to 2.5%, and one or two of V and Nb are V + 1 / 2Nb: 0.3 to 1.0% the has free and excellent balance in wear resistance characterized by comprising Fe and unavoidable impurities, and crushing tool steel which suppresses aging.
(2) Using the steel described in (1) above, cutting into a blade shape, quenching, and then performing high-temperature tempering at 550 to 600 ° C. twice or more to reduce the amount of retained austenite to 1.0% or less. It exists in the manufacturing method of the crushing blade which suppressed the secular change characterized by having performed.
以上述べたように、本発明による基本成分の見直しと熱処理の実施によって、低コストで早期割れや欠けを抑制した長寿命な破砕用刃物用鋼およびそれを使用した破砕刃の製造方法を提供することが可能となった。 As described above, by reviewing the basic components and carrying out heat treatment according to the present invention, a long-life steel for blades for crushing that suppresses early cracking and chipping at low cost and a method for producing a crushing blade using the same are provided. It became possible.
以下、本発明に係る成分組成の限定理由について説明する。
Ｃ：０．３〜０．５％
Ｃは、焼入れ焼戻し後の硬度を確保するために、０．３％以上必要である。また、Ｃｒ，Ｍｏ，Ｖ，Ｗ，Ｎｂなどの合金元素と結合して炭化物を形成し、耐摩耗性に寄与するが、しかし、添加し過ぎると炭化物が粗大になり靱性を著しく劣化させるため、その上限を０．５％とした。好ましくは０．４〜０．５％とする。
Hereinafter, the reasons for limiting the component composition according to the present invention will be described.
C: 0.3-0.5%
C is required to be 0.3% or more in order to ensure the hardness after quenching and tempering. In addition, it combines with alloy elements such as Cr, Mo, V, W, Nb to form carbides and contributes to wear resistance. However, if added too much, the carbides become coarse and the toughness deteriorates significantly. The upper limit was 0.5%. Preferably it is 0.4 to 0.5%.
Ｓｉ：０．２〜０．５％
Ｓｉは、製鋼における脱酸剤として添加する。また、焼入れ性にも有効であるため、少なくとも０．２％は必要である。また、添加量の増加に伴って、ミクロ偏析が増加し焼戻脆性が助長されて靱性が低下するだけでなく、焼入れ焼戻し後の残留オーステナイトを増加させ、経年変化を大きくするため、添加する上限を０．５％とした。すなわち、Ｓｉ添加量の増加により、焼戻し時のセメンタイトの析出が遅くなり、残留オーステナイトが分解しにくくなった結果、分解途上の不安定なオーステナイトが多く残存し、これが使用開始後に分解して経年変化を大きくしている。
Si: 0.2 to 0.5%
Si is added as a deoxidizer in steelmaking. Moreover, since it is effective also for hardenability, at least 0.2% is required. In addition, as the amount added increases, microsegregation increases, temper brittleness is promoted and toughness decreases, and the retained austenite after quenching and tempering is increased, and the secular change is increased. Was 0.5%. In other words, the increase in the amount of Si added slows the precipitation of cementite during tempering, making it difficult for the retained austenite to decompose. Has increased.
Ｍｎ：０．１〜１．０％
Ｍｎは、Ｓｉと同様に脱酸剤として添加し、焼入性にも有効であるため、０．１％以上添加する必要があるが、しかし、添加し過ぎると靱性を劣化させるため、その上限を１．０％とした。好ましくは０．３〜０．７％とする。
Mn: 0.1 to 1.0%
Mn is added as a deoxidizer in the same way as Si, and is effective for hardenability. Therefore, it is necessary to add 0.1% or more. However, if added too much, the toughness is deteriorated. Was 1.0%. Preferably it is 0.3 to 0.7%.
Ｃｒ：４．０〜６．０％
Ｃｒは、焼入性と耐摩耗性を確保するために、４．０％以上必要である。特に破砕用刃物のような大型刃物では焼入時の内部での冷却が遅いため、焼入性が悪い場合には、硬さが低くなりオーステナイトが多く残存してしまい、使用開始後に経年変化により内部で引張り残留応力が高まり、早期破壊の原因となることがある。また、添加し過ぎると一次炭化物の粗大化して著しく靱性が悪化するため、その上限を６．０％とした。好ましくは５．０〜６．０％とする。
Cr: 4.0-6.0%
Cr needs to be 4.0% or more in order to ensure hardenability and wear resistance. Especially for large blades such as crushing blades, the internal cooling at the time of quenching is slow, so if the hardenability is poor, the hardness will be low and a lot of austenite will remain. Internal tensile residual stress increases, which may cause premature failure. Moreover, since an excessive addition will coarsen a primary carbide and toughness will deteriorate remarkably, the upper limit was made 6.0%. Preferably it is 5.0 to 6.0%.
Ｍｏ＋１／２Ｗ：０．８〜２．５％
Ｍｏ＋１／２Ｗは、焼入性確保と析出炭化物による耐摩耗性改善のために、０．８％以上必要である。しかし、添加し過ぎると析出炭化物の凝集が顕著になり、靱性が低下するだけでなく、経年変化が大きくなるため、その上限を２．５％とした。好ましくは１．２〜２．０％とする。
Mo + 1 / 2W: 0.8-2.5%
Mo + 1 / 2W is required to be 0.8% or more in order to ensure hardenability and improve wear resistance due to precipitated carbides. However, if added too much, the agglomeration of precipitated carbides becomes remarkable and not only the toughness decreases, but also the secular change increases, so the upper limit was made 2.5%. Preferably, the content is 1.2 to 2.0%.
Ｖ＋１／２Ｎｂ：０．３〜１．０％ Ｖ＋１／２Ｎｂは、微細で硬質な炭化物の分散析出による耐摩耗性改善のために、０．３％以上必要である。しかし、添加し過ぎると炭化物が粗大になり、靱性が低下するだけでなく、高温焼戻し時の熱処理変寸法が大きくなるため、その上限を１．０％とした。好ましくは０．５〜１．０％とする。 V + 1 / 2Nb: 0.3 to 1.0% V + 1 / 2Nb is required to be 0.3% or more in order to improve wear resistance by dispersion and precipitation of fine and hard carbides. However, if added too much, the carbide becomes coarse and not only the toughness is lowered, but also the heat treatment deformed dimension at high temperature tempering becomes large, so the upper limit was made 1.0%. Preferably, the content is 0.5 to 1.0%.
残留オーステナイト量：１．０％以下
残留オーステナイト量を規制したのは、残留オーステナイトの分解による経年変化と残留応力の増加を最小限に抑えて、使用前のクリアランスを確保するために必要である。そのためには、０．１％以下とする必要がある。
Residual austenite amount: 1.0% or less The amount of retained austenite is regulated in order to minimize a secular change and an increase in residual stress due to decomposition of retained austenite, and to ensure clearance before use. For that purpose, it is necessary to make it 0.1% or less.
以下、本発明について実施例によって具体的に説明する。
表１に示す成分組成の鋼を、それぞれ１ｔ真空溶解炉にて出鋼し、造塊後、φ１５０に圧延した後、８００〜８８０℃保持から徐冷による焼鈍しを行った。その棒鋼から各種試験片を割り出し後、焼入れ焼戻しを行い、各種試験を実施した。なお、試験片の焼入れは鋼種ＡとＥのみ８５０℃保持から油冷、他は１０３０℃保持から空冷で行い、焼戻しは表２に示した条件で、それぞれ実施した。なお、耐摩耗性は大越式摩耗試験（試験片サイズ：１５×２０×５ｍｍ）により摩擦距離２００ｍ、最終荷重６１．７Ｎ、摩擦速度２．４４ｍ／ｓで摩耗量を測定した。また、靱性はシャルピー衝撃値（試験片はφ２５、再鍛伸材中心部圧延方向より割り出し）により評価した。
Hereinafter, the present invention will be specifically described with reference to examples.
Steels having the component compositions shown in Table 1 were each produced in a 1 t vacuum melting furnace, ingot, rolled to φ150, and then annealed by annealing from 800 to 880 ° C. Various test pieces were indexed from the steel bar, and then quenched and tempered, and various tests were performed. In addition, quenching of the test pieces was performed only for steel types A and E by holding from 850 ° C. to oil cooling, and from others by holding from 1030 ° C. to air cooling, and tempering was performed under the conditions shown in Table 2. In addition, the abrasion resistance was measured by the Ogoshi type abrasion test (test piece size: 15 × 20 × 5 mm) at a friction distance of 200 m, a final load of 61.7 N, and a friction speed of 2.44 m / s. Further, toughness was evaluated by Charpy impact value (the test piece was φ25, indexed from the rolling direction of the re-forged material center part).
上述したような成分組成を有する鋼の焼戻温度条件、焼入れ焼戻し硬さ、ならびにその場合の比摩耗量およびシャルピー衝撃値を示したものが表２である。Ｎｏ．１〜６に示す比較例はいずれも表１に示す比較鋼であって、しかも焼戻温度が低いか２回目の高温焼戻しを行っていない場合である。いずれの場合も比摩耗量が高いかシャルピー衝撃値が低い値を示していることが分かる。これに対し、本発明であるＮｏ．７〜１８は、いずれも本発明の条件を満たしていることから、比摩耗量も少なく、かつシャルピー衝撃値の高い値を示している。 Table 2 shows the tempering temperature conditions, quenching and tempering hardness, and the specific wear amount and Charpy impact value of the steel having the above component composition. No. The comparative examples shown in 1 to 6 are all comparative steels shown in Table 1, and the tempering temperature is low or the second high temperature tempering is not performed. In any case, it can be seen that the specific wear amount is high or the Charpy impact value is low. On the other hand, No. which is the present invention. Since Nos. 7 to 18 all satisfy the conditions of the present invention, the specific wear amount is small and the Charpy impact value is high.
さらに、経年変化測定試験片（直径１４０ｍｍ、長さ８０ｍｍ）を作製し、焼入れ焼戻しを実施した２４時間後にＸ線回折法による残留オーステナイト測定および径方向と圧延方向における寸法測定を行い、それを２ケ月放置した後に再度寸法測定を行い、経年変化率を算出して、経年変化特性を評価した。表３に示すように、本発明鋼で所定の温度での焼戻を実施することによって、残留オーステナイトを１．０％以下にまで低減し、経年変化を大幅に抑制できることが分かる。 Further, a secular change measurement specimen (diameter 140 mm, length 80 mm) was prepared, and after 24 hours after quenching and tempering, residual austenite measurement by X-ray diffraction method and dimension measurement in the radial direction and the rolling direction were performed. After being left for months, the dimensions were measured again, the aging rate was calculated, and the aging characteristics were evaluated. As shown in Table 3, it can be seen that by carrying out tempering at a predetermined temperature with the steel of the present invention, the retained austenite can be reduced to 1.0% or less and the secular change can be significantly suppressed.
特許出願人 山陽特殊製鋼株式会社
代理人 弁理士 椎 名 彊
Patent Applicant Sanyo Special Steel Co., Ltd.
Attorney: Attorney Shiina
Claims (2)
Ｃ：０．３〜０．５％、
Ｓｉ：０．２〜０．５％、
Ｍｎ：０．１〜１．０％、
Ｃｒ：４．０〜６．０％、
ＭｏおよびＷの内の１種または２種をＭｏ＋１／２Ｗ：０．８〜２．５％、
ＶおよびＮｂの内の１種または２種をＶ＋１／２Ｎｂ：０．３〜１．０％、
を含有し、残部をＦｅと不可避的不純物からなることを特徴とする耐摩耗性に優れ、かつ経年変化を抑制した破砕用刃物用鋼。 % By mass
C: 0.3-0.5%
Si: 0.2 to 0.5%
Mn: 0.1 to 1.0%,
Cr: 4.0-6.0%,
One or two of Mo and W are Mo + 1 / 2W: 0.8 to 2.5%,
One or two of V and Nb are V + 1 / 2Nb: 0.3-1.0%,
The has free and excellent balance in wear resistance characterized by comprising Fe and unavoidable impurities, and crushing tool steel which suppresses aging.
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