JPH04358046A - High speed steel base sintered alloy - Google Patents
High speed steel base sintered alloyInfo
- Publication number
- JPH04358046A JPH04358046A JP14700991A JP14700991A JPH04358046A JP H04358046 A JPH04358046 A JP H04358046A JP 14700991 A JP14700991 A JP 14700991A JP 14700991 A JP14700991 A JP 14700991A JP H04358046 A JPH04358046 A JP H04358046A
- Authority
- JP
- Japan
- Prior art keywords
- sintered alloy
- speed steel
- toughness
- less
- alloy
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Granted
Links
- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 47
- 239000000956 alloy Substances 0.000 title claims abstract description 47
- 229910000997 High-speed steel Inorganic materials 0.000 title claims abstract description 22
- 239000011159 matrix material Substances 0.000 claims abstract description 10
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 7
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 6
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 6
- 229910052721 tungsten Inorganic materials 0.000 claims abstract description 6
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 5
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 5
- 229910052748 manganese Inorganic materials 0.000 claims abstract 3
- 229910052742 iron Inorganic materials 0.000 claims description 2
- 229910052759 nickel Inorganic materials 0.000 abstract 1
- 230000000694 effects Effects 0.000 description 27
- 238000000034 method Methods 0.000 description 19
- 150000001247 metal acetylides Chemical class 0.000 description 15
- 238000005245 sintering Methods 0.000 description 15
- 239000000463 material Substances 0.000 description 12
- 238000005496 tempering Methods 0.000 description 11
- 239000007789 gas Substances 0.000 description 8
- 238000005452 bending Methods 0.000 description 7
- 238000010438 heat treatment Methods 0.000 description 7
- 230000008569 process Effects 0.000 description 7
- 229910000831 Steel Inorganic materials 0.000 description 6
- 230000007797 corrosion Effects 0.000 description 6
- 238000005260 corrosion Methods 0.000 description 6
- 238000002844 melting Methods 0.000 description 6
- 230000008018 melting Effects 0.000 description 6
- 239000000203 mixture Substances 0.000 description 6
- 238000010791 quenching Methods 0.000 description 6
- 230000000171 quenching effect Effects 0.000 description 6
- 238000005096 rolling process Methods 0.000 description 6
- 239000010959 steel Substances 0.000 description 6
- 230000000052 comparative effect Effects 0.000 description 5
- 230000007423 decrease Effects 0.000 description 5
- 239000000843 powder Substances 0.000 description 5
- 229910001566 austenite Inorganic materials 0.000 description 4
- 238000001513 hot isostatic pressing Methods 0.000 description 4
- 230000006872 improvement Effects 0.000 description 4
- 238000004519 manufacturing process Methods 0.000 description 4
- 230000004888 barrier function Effects 0.000 description 3
- 238000001816 cooling Methods 0.000 description 3
- 239000007791 liquid phase Substances 0.000 description 3
- 229910000734 martensite Inorganic materials 0.000 description 3
- 239000002245 particle Substances 0.000 description 3
- 238000001556 precipitation Methods 0.000 description 3
- 229920006395 saturated elastomer Polymers 0.000 description 3
- 230000035939 shock Effects 0.000 description 3
- 239000000126 substance Substances 0.000 description 3
- 229910001563 bainite Inorganic materials 0.000 description 2
- 239000002775 capsule Substances 0.000 description 2
- 239000000470 constituent Substances 0.000 description 2
- 230000006866 deterioration Effects 0.000 description 2
- 238000003754 machining Methods 0.000 description 2
- 239000002184 metal Substances 0.000 description 2
- 229910052751 metal Inorganic materials 0.000 description 2
- 238000004663 powder metallurgy Methods 0.000 description 2
- 238000007670 refining Methods 0.000 description 2
- -1 2C type Chemical class 0.000 description 1
- 229910000851 Alloy steel Inorganic materials 0.000 description 1
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 1
- 229910001209 Low-carbon steel Inorganic materials 0.000 description 1
- 229910001182 Mo alloy Inorganic materials 0.000 description 1
- 229910003296 Ni-Mo Inorganic materials 0.000 description 1
- 230000009471 action Effects 0.000 description 1
- 230000008901 benefit Effects 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 230000008094 contradictory effect Effects 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 238000002425 crystallisation Methods 0.000 description 1
- 230000008025 crystallization Effects 0.000 description 1
- 239000006185 dispersion Substances 0.000 description 1
- 230000001747 exhibiting effect Effects 0.000 description 1
- 238000005098 hot rolling Methods 0.000 description 1
- 229910052739 hydrogen Inorganic materials 0.000 description 1
- 239000001257 hydrogen Substances 0.000 description 1
- 239000007769 metal material Substances 0.000 description 1
- 239000012071 phase Substances 0.000 description 1
- 238000013001 point bending Methods 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 238000004881 precipitation hardening Methods 0.000 description 1
- 238000003825 pressing Methods 0.000 description 1
- 239000003507 refrigerant Substances 0.000 description 1
- 230000000717 retained effect Effects 0.000 description 1
- 238000007788 roughening Methods 0.000 description 1
- 150000003839 salts Chemical class 0.000 description 1
- 238000001878 scanning electron micrograph Methods 0.000 description 1
- 239000007787 solid Substances 0.000 description 1
- 230000000087 stabilizing effect Effects 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
Abstract
Description
【０００１】0001
【産業上の利用分野】本発明は、高耐摩耗性と高靭性が
要求される用途、例えば鋼材圧延用ロール等の構成材料
として有用な高速度鋼系焼結合金に関する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a high-speed steel-based sintered alloy useful for applications requiring high wear resistance and high toughness, for example, as a constituent material of steel rolling rolls and the like.
【０００２】0002
【従来の技術】高速度鋼は、焼入れ・焼もどしの調質熱
処理により、マルテンサイトまたはベイナイトの硬質の
基地に、ＭＣ型、Ｍ２Ｃ型、Ｍ６Ｃ型等の炭化物が微細
に分散混在した組織が与えられ、その硬質の基地と、炭
化物の分散強化作用とによる極めて硬質で高度の摩耗抵
抗性を備えた合金である。[Prior Art] High-speed steel is given a microstructure in which carbides of MC type, M2C type, M6C type, etc. are finely dispersed in a hard base of martensite or bainite through heat treatment such as quenching and tempering. It is an extremely hard alloy with a high degree of wear resistance due to its hard matrix and the dispersion strengthening effect of carbides.
【０００３】高速度鋼の製造法については、従来の溶解
法のほかに、近時は粉末冶金の手法を用い焼結合金とし
て製造することも行われている。粉末冶金法によれば、
溶解法では製造できないような成分構成を有する合金の
製造も可能となり、成分設計の自由度が大きく、また焼
結手段として熱間等方圧加圧焼結（ＨＩＰ）法を適用し
、高加圧力の均一な作用下に焼結を行わせることにより
、高緻密質で均質性にすぐれた焼結合金を得ることがで
きる。Regarding the manufacturing method of high-speed steel, in addition to the conventional melting method, recently, powder metallurgy techniques have been used to manufacture the steel as a sintered alloy. According to the powder metallurgy method,
It is now possible to manufacture alloys with compositions that cannot be manufactured using the melting method, allowing a greater degree of freedom in composition design, and by applying the hot isostatic pressing (HIP) method as a sintering method, it is possible to By performing sintering under the uniform effect of pressure, a highly dense sintered alloy with excellent homogeneity can be obtained.
【０００４】高速度鋼系合金の用途は広く、例えば鋼材
圧延用ロールについて、その耐用寿命の向上および被圧
延材の表面品質改善等を目的とし、ロール胴部表面に高
速度鋼系焼結合金層を形成して耐摩耗性を高めること等
も提案されている（特開昭６３−２９７５１０号，特開
平３−４７６０９号等）。[0004] High-speed steel alloys have a wide range of uses. For example, high-speed steel-based sintered alloys are used on the surface of the roll body for the purpose of increasing the service life of rolls for rolling steel materials and improving the surface quality of the rolled material. It has also been proposed to improve wear resistance by forming a layer (JP-A-63-297510, JP-A-3-47609, etc.).
【０００５】[0005]
【発明が解決しようとする課題】高速度鋼系合金を耐摩
耗用途、就中鋼材圧延用ロール等のように高荷重の負担
による曲げ応力や熱的・機械的衝撃が繰返し加わる部材
の耐久性・安定性の改善を目的として適用する場合、そ
の高速度鋼系合金は、耐摩耗性だけでなく、部材に加わ
る高荷重や衝撃によるクラック発生とその伝播を抑制し
得る高度の靭性を具備したものであることが要求される
。しかるに、耐摩耗性と靭性とは一般に相反的な材料特
性であり、高耐摩耗性と高靭性とを同時に充足させるこ
とは容易でない。本発明は上記に鑑みてなされたもので
あり、圧延ロール等のように高耐摩耗性と高靭性とが要
求される部材の構成材料として有用な高速度鋼系焼結合
金を提供する。[Problem to be solved by the invention] High-speed steel alloys are used for wear-resistant applications, especially durability of members that are repeatedly subjected to bending stress and thermal/mechanical shock due to high loads, such as rolls for rolling steel materials.・When applied for the purpose of improving stability, the high-speed steel alloy has not only wear resistance but also a high degree of toughness that can suppress the occurrence and propagation of cracks due to high loads and impacts applied to the member. It is required that it be a thing. However, wear resistance and toughness are generally contradictory material properties, and it is not easy to simultaneously satisfy high wear resistance and high toughness. The present invention has been made in view of the above, and provides a high-speed steel-based sintered alloy useful as a constituent material of members such as rolling rolls that require high wear resistance and high toughness.
【０００６】[0006]
【課題を解決するための手段および作用】本発明の高速
度鋼系焼結合金は、Ｃ：１．７〜３．５％，Ｓｉ：０．
４％以下（または、０．６〜３．５％），Ｍｎ：０．４
％以下，Ｃｒ：３〜２０％，Ｖ，Ｔｉ，Ｎｂのいずれか
１種ないし２種以上の元素：１２％以下，Ｗ：５〜１４
％，Ｍｏ：３〜９％，Ｃｏ：７〜１４％，残部実質的に
Ｆｅ（所望によりＢ：２％以下，Ｎｉ：３％以下の１種
もしくは２種を含有）からなり、基地中に、粒径１０〜
５０μｍの炭化物粒が均一に分散し、その面積率は１０
〜５０％であることを特徴としている。以下、本発明に
ついて詳しく説明する。[Means and effects for solving the problems] The high speed steel sintered alloy of the present invention has C: 1.7 to 3.5%, Si: 0.
4% or less (or 0.6 to 3.5%), Mn: 0.4
% or less, Cr: 3-20%, any one or more elements of V, Ti, Nb: 12% or less, W: 5-14
%, Mo: 3 to 9%, Co: 7 to 14%, the remainder substantially consisting of Fe (containing one or two of B: 2% or less and Ni: 3% or less, if desired), and the base contains , particle size 10~
Carbide grains of 50 μm are uniformly dispersed, and the area ratio is 10
~50%. The present invention will be explained in detail below.
【０００７】本発明の高速度鋼系焼結合金の化学組成限
定理由は次のとおりである。
Ｃ：１．７〜３．５％
ＣはＶ、Ｗ、Ｍｏ等と結合して、ＭＣ型、Ｍ６Ｃ型、Ｍ
２Ｃ型等の炭化物を形成し、合金の高度を高める。この
効果を十分ならしめるため、含有量の下限を１．７％と
する。しかし、Ｃの増量は反面において、炭化物の過剰
析出による合金の靭性劣化および加工性の低下等の原因
となる。このため、３．５％を上限とする。The reason for limiting the chemical composition of the high-speed steel sintered alloy of the present invention is as follows. C: 1.7-3.5% C combines with V, W, Mo, etc. to form MC type, M6C type, M
Forms carbides such as 2C type, increasing the alloy's sophistication. In order to make this effect sufficient, the lower limit of the content is set to 1.7%. However, on the other hand, increasing the amount of C causes deterioration of the toughness of the alloy and deterioration of workability due to excessive precipitation of carbides. Therefore, the upper limit is set at 3.5%.
【０００８】Ｓｉ：０．４％以下、または０．６〜３．
５％
Ｓｉは焼入れ性改善に奏効する。また、添加量の増加に
より耐孔食性改善効果が得られる。焼入れ性改善効果は
０．４％までの添加で十分であり、それを越える添加の
必要はない。従って焼入れ性改善のための添加量は０．
４％までとする。耐孔食性改善効果は０．６％以上の添
加により現れる。従って焼入れ性改善と耐孔食性の改善
を望む場合の添加量は０．６％以上とする。添加増量に
より効果を増すが、反面靭性の低下を招き、曲げ荷重や
熱的・機械的衝撃に対する抵抗性の不足をきたすので、
３．５％を上限とする。[0008]Si: 0.4% or less, or 0.6 to 3.
5% Si is effective in improving hardenability. In addition, the effect of improving pitting corrosion resistance can be obtained by increasing the amount added. Addition of up to 0.4% is sufficient for the hardenability improvement effect, and there is no need to add more than that. Therefore, the amount added to improve hardenability is 0.
Up to 4%. The effect of improving pitting corrosion resistance appears when 0.6% or more is added. Therefore, when it is desired to improve hardenability and pitting corrosion resistance, the amount added should be 0.6% or more. Increasing the amount added increases the effect, but on the other hand, it causes a decrease in toughness, resulting in a lack of resistance to bending loads and thermal/mechanical shock.
The upper limit is 3.5%.
【０００９】Ｍｎ：０．４％以下
Ｍｎは脱酸作用を有し、また焼入れ性の改善効果を有す
る。この効果を得るための添加量は０．４％までで十分
であり、多量の添加は高温におけるオーステナイト粒の
粗大化を招き、合金の脆化の原因となる。このため、０
．４％を上限とした。Mn: 0.4% or less Mn has a deoxidizing effect and also has the effect of improving hardenability. It is sufficient to add up to 0.4% to obtain this effect, and addition of a large amount leads to coarsening of austenite grains at high temperatures, causing embrittlement of the alloy. For this reason, 0
．． The upper limit was set at 4%.
【００１０】Ｃｒ：３〜２０％
Ｃｒは合金の焼入れ性を改善し、また焼もどし軟化抵抗
性を高める。更に、その添加増量により、耐孔食性向上
効果が得られる。焼入れ性、および焼もどし軟化抵抗性
の改善効果は３％以上の添加により得られ、その効果は
６％までの添加でほぼ飽和する。耐孔食性改善効果は６
．５％以上の添加により現れる。従って、焼入れ性およ
び焼もどし軟化抵抗性の改善と併せて耐孔食性改善効果
を望む場合の添加量は６．５％を下限とする。添加量の
増加によりその効果を増すが、その反面、熱間圧延ロー
ルの用途では、赤熱鋼材に対する焼付抵抗性が減じ、ま
たロール表面の耐肌荒れ性が低下するので、２０％を上
限とし、好ましくは１５％までとする。Cr: 3-20% Cr improves the hardenability of the alloy and also increases its resistance to temper softening. Furthermore, by increasing the amount added, the effect of improving pitting corrosion resistance can be obtained. The effect of improving hardenability and temper softening resistance can be obtained by adding 3% or more, and the effect is almost saturated by adding up to 6%. Pitting corrosion resistance improvement effect is 6
．． Appears when 5% or more is added. Therefore, if an improvement in pitting corrosion resistance is desired in addition to improvement in hardenability and temper softening resistance, the lower limit of the amount added should be 6.5%. Increasing the amount added increases the effect, but on the other hand, in applications for hot rolling rolls, the seizing resistance to red-hot steel materials and the roughening resistance of the roll surface decreases, so the upper limit is preferably 20%. shall be up to 15%.
【００１１】Ｖ，Ｔｉ，Ｎｂ：１２％以下Ｖ，Ｔｉ，Ｎ
ｂは焼入れ後の焼もどし処理により、微細なＭＣ型炭化
物として析出し顕著な二次硬化をもたらし、また焼もど
し軟化抵抗性を示す。更に、Ｖは焼結合金組織を微細化
し靭性等の機械的性質を高める。しかし、多量の添加は
靭性の低下を招き、また切削加工性等を悪くするので、
１２％を上限とする。２種または３種の元素を複合添加
する場合は、その合計量を１２％以下とする。[0011] V, Ti, Nb: 12% or less V, Ti, N
b is precipitated as fine MC-type carbides by tempering treatment after quenching, resulting in significant secondary hardening and exhibiting resistance to tempering softening. Furthermore, V refines the sintered alloy structure and improves mechanical properties such as toughness. However, adding too much leads to a decrease in toughness and poor machinability, so
The upper limit is 12%. When adding two or three types of elements in combination, the total amount should be 12% or less.
【００１２】Ｗ：５〜１４％
Ｗは強力な炭化物形成元素であり、焼もどし処理により
微細なＭ６Ｃ型炭化物として析出し二次硬化をもたらす
。また焼もどし軟化抵抗性を示す。添加量の下限を５％
としたのは、その炭化物の析出による十分な二次硬化を
得るためである。添加増量により、その効果を増すが、
反面靭性等の機械的性質の低下を招くので、１４％を上
限とした。W: 5 to 14% W is a strong carbide-forming element, and upon tempering, it precipitates as fine M6C type carbides and causes secondary hardening. It also shows resistance to temper softening. Lower limit of addition amount to 5%
The reason for this is to obtain sufficient secondary hardening due to the precipitation of carbides. The effect increases by increasing the amount added, but
On the other hand, it causes a decrease in mechanical properties such as toughness, so the upper limit was set at 14%.
【００１３】Ｍｏ：３〜９％
Ｍｏは焼入れ性を高めると共に、焼もどし処理により微
細なＭ２Ｃ型炭化物を形成して二次硬化を生起し、高温
硬さの保持に奏効する。この効果は３％以上の添加によ
り得られる。しかし９％をこえるとその効果はほぼ飽和
するので９％までとする。Mo: 3-9% Mo not only improves hardenability, but also forms fine M2C type carbides during tempering treatment to cause secondary hardening, and is effective in maintaining high-temperature hardness. This effect can be obtained by adding 3% or more. However, if it exceeds 9%, the effect is almost saturated, so it is limited to 9%.
【００１４】Ｃｏ：７〜１４％
Ｃｏは、焼もどし処理による炭化物の析出と、マトリッ
クスの二次マルテンサイト化による焼結合金の強化を助
長すると共に、高温硬さの向上に奏効する。この効果は
７％以上の添加により得られる。しかし、１４％をこえ
るとその効果はほぼ飽和するので１４％を上限とする。Co: 7 to 14% Co promotes the precipitation of carbides during tempering and strengthens the sintered alloy through secondary martensite formation of the matrix, and is effective in improving high-temperature hardness. This effect can be obtained by adding 7% or more. However, if it exceeds 14%, the effect is almost saturated, so 14% is set as the upper limit.
【００１５】Ｂ：２％以下
Ｂは、Ｃ代替元素であり、ほう化物を形成して耐摩耗性
の向上に寄与する。２％のＢは１％のＣに等価である。
また基地中に固溶して基地を強化する。しかしし、多量
の添加は、合金の融点を下げ、強度の低下の原因となる
ので、２％を上限とする。B: 2% or less B is an element replacing C, forms a boride, and contributes to improving wear resistance. 2% B is equivalent to 1% C. It also strengthens the base by dissolving it into the base. However, addition of a large amount lowers the melting point of the alloy and causes a decrease in strength, so the upper limit is set at 2%.
【００１６】Ｎｉ：３％以下
Ｎｉは、オーステナイト相安定化元素であり、残留オー
ステナイト量の増加による靭性の改善に奏効する。しか
し、オーステナイト量の増加は、反面において機械加工
の困難化を招くので、３％を越えてはならない。Ni: 3% or less Ni is an austenite phase stabilizing element and is effective in improving toughness by increasing the amount of retained austenite. However, since an increase in the amount of austenite makes machining difficult, it should not exceed 3%.
【００１７】本発明の高速度鋼系焼結合金は、粒径１０
〜５０μｍの比較的粗粒の炭化物が基地中に分散した組
織を有する。その粗粒炭化物は後記のように焼結処理工
程において液相からの晶出炭化物として形成することが
できる。The high speed steel sintered alloy of the present invention has a grain size of 10
It has a structure in which relatively coarse grained carbides of ~50 μm are dispersed throughout the matrix. The coarse carbide can be formed as carbide crystallized from the liquid phase during the sintering process as described below.
【００１８】基地中に分散する上記の粗粒炭化物粒の存
在により、焼結合金のクラック伝播に対する抵抗性が高
められる。すなわち、焼結合金の実使用においてクラッ
クが生じた場合、クラックの伝播は基地中に分散した粗
粒の炭化物との衝突により、前方への伝播が阻まれ、ま
たそのクラックが炭化物粒を越えて前方に伝播するには
炭化物粒を裂割させねばならないので、それに伴ってク
ラックの伝播エネルギが効果的に減殺される。このよう
に、基地中に分散する粗粒の炭化物粒はクラックの伝播
を抑制・阻止する障壁として機能する。The presence of the coarse carbide grains dispersed in the matrix increases the resistance of the sintered alloy to crack propagation. In other words, when a crack occurs in the actual use of a sintered alloy, the propagation of the crack is blocked by collision with the coarse carbide grains dispersed in the matrix, and the crack also crosses the carbide grains. Since the carbide grains must be split in order to propagate forward, the propagation energy of the crack is effectively reduced accordingly. In this way, the coarse carbide grains dispersed in the matrix function as a barrier that suppresses and prevents the propagation of cracks.
【００１９】上記炭化物の粒径を１０μｍ以上としたの
は、クラックの伝播に対する障壁効果を確保するためで
あり、またその粗粒炭化物粒の基地中に占める割合を面
積率で１０％以上としたのは、それに満たないと、炭化
物粒の障壁効果によるクラック伝播抵抗性の改善効果が
不足するからである。より好ましくは２０％以上である
。The grain size of the carbide is set to 10 μm or more in order to ensure a barrier effect against the propagation of cracks, and the proportion of the coarse carbide grains in the matrix is set to 10% or more in terms of area ratio. This is because if it is less than this, the effect of improving crack propagation resistance due to the barrier effect of carbide grains will be insufficient. More preferably, it is 20% or more.
【００２０】なお、粗粒炭化物粒の粒径の上限を５０μ
ｍとし、面積率を５０％までとしたのは、クラック伝播
の抵抗性改善効果の点から、それ以上とする利益がない
だけでなく、却って焼結合金の脆化傾向を招くからであ
る。[0020] The upper limit of the grain size of the coarse carbide grains is 50 μm.
The reason why the area ratio is set to m and the area ratio is set to 50% is that not only is there no benefit in increasing the crack propagation resistance from the viewpoint of improving the crack propagation resistance, but it also causes a tendency for the sintered alloy to become brittle.
【００２１】本発明の焼結合金を製造するための焼結手
法は任意であるが、好ましくは熱間等方圧加圧焼結法（
ＨＩＰ焼結法）が適用される。ＨＩＰ焼結法によれば、
高加圧力（例えば８００ｋｇｆ ／ｃｍ２以上）の均
一な作用下に高緻密質の焼結合金を得ることができる。
なお、合金粉末が比較的多量の酸化皮膜を付随するもの
である場合は、水素含有ガス等の還元ガスを使用し加熱
下に酸化皮膜を還元除去したうえで焼結を行うようにす
ればよい。本発明ではその焼結処理を、液相が共存する
温度域において行う。その焼結処理過程において、液相
から前述の粗粒サイズの炭化物を晶出形成することがで
きる。このための焼結処理温度は、絶対温度（°Ｋ）で
表示した融点の約９０〜９５％の温度域〔例えば、融点
が１３２０℃（＝１５９３°Ｋ）の場合は、１４３２°
Ｋ（＝１５９３°Ｋ×０．９）〜１５１３°Ｋ（＝１５
９３°Ｋ×０．９５）の温度域〕が好適である。その処
理時間は、粗粒炭化物粒の不足または過剰生成をきたす
ことなく所定の焼結が達成されるように、処理温度や加
圧力等に応じて設定されるが、概ね２〜４Ｈｒの処理と
してよい。Although any sintering method can be used to produce the sintered alloy of the present invention, the hot isostatic pressure sintering method (
HIP sintering method) is applied. According to the HIP sintering method,
A highly dense sintered alloy can be obtained under the uniform action of a high pressure (for example, 800 kgf/cm2 or more). If the alloy powder is accompanied by a relatively large amount of oxide film, the oxide film may be reduced and removed under heating using a reducing gas such as a hydrogen-containing gas before sintering. . In the present invention, the sintering process is performed in a temperature range where a liquid phase coexists. During the sintering process, the aforementioned coarse-grained carbides can be crystallized from the liquid phase. The sintering temperature for this purpose is approximately 90 to 95% of the melting point expressed in absolute temperature (°K) [for example, if the melting point is 1320°C (=1593°K), 1432°C
K (=1593°K×0.9) ~ 1513°K (=15
A temperature range of 93°K×0.95) is suitable. The treatment time is set according to the treatment temperature, pressing force, etc. so that the desired sintering is achieved without causing a shortage or excessive production of coarse carbide grains, but the treatment time is generally 2 to 4 hours. good.
【００２２】焼結処理後、調質のための熱処理（焼入れ
・焼もどし処理）を行う。その熱処理は高速度鋼系合金
製造の常法に従って行えばよい。すなわち、焼入れ処理
は、例えば温度約１０５０〜１２５０℃に加熱保持した
のち、油浴または塩浴を使用し、あるいはガス（Ｎ２ガ
ス等）を冷媒として行えばよく、また焼もどし処理は、
例えば温度約５００〜６００℃に適当時間（例えば５〜
１０Ｈｒ）保持したのち、徐冷（空冷等）する操作を１
回ないしは複数回（例えば２〜４回）実施することによ
り達成することができる。After the sintering process, heat treatment (quenching/tempering process) for refining is performed. The heat treatment may be carried out in accordance with conventional methods for producing high-speed steel alloys. That is, the quenching treatment may be performed by heating and maintaining the temperature at about 1050 to 1250°C, for example, using an oil bath or salt bath, or using a gas (N2 gas, etc.) as a refrigerant, and the tempering treatment can be performed by
For example, at a temperature of about 500 to 600℃ for an appropriate time (for example, 5 to 600℃)
After holding for 10 hours, perform gradual cooling (air cooling, etc.)
This can be achieved by carrying out the procedure once or multiple times (for example, 2 to 4 times).
【００２３】本発明の高速度鋼系焼結合金は、上記調質
熱処理が施されて、マルテンサイトまたはベイナイトの
基地に、前記晶出炭化物として成形された粒径１０〜５
０μｍの粗粒炭化物、焼もどしでの二次炭化物として析
出した微細炭化物粒が混在分散した組織となり、その微
細炭化物の分散硬化作用による高硬度・高耐摩耗性と、
粗粒炭化物のクラック伝播抵抗性による高靭性とがもた
らされる。なお、基地中の炭化物粒の総量は面積率約１
５〜５５％程度である。The high-speed steel-based sintered alloy of the present invention is subjected to the above-mentioned refining heat treatment, and has a grain size of 10 to 5 formed as the crystallized carbide on the martensite or bainite base.
The structure is a mixture of 0μm coarse carbide and fine carbide grains precipitated as secondary carbide during tempering, resulting in high hardness and high wear resistance due to the dispersion hardening effect of the fine carbide.
High toughness is provided by the crack propagation resistance of coarse carbides. In addition, the total amount of carbide grains in the base has an area ratio of approximately 1
It is about 5 to 55%.
【００２４】本発明の高速度鋼系焼結合金の用途は多岐
に亘るが、耐摩耗性等は部材の表面の問題であるので、
例えば圧延用ロールの胴部に本発明の焼結合金を適用す
る場合には、適当な金属材料（例えは、ＪＩＳ Ｇ
４１０５ のＣｒ−Ｍｏ系合金鋼、同４１０３のＣ
ｒ−Ｎｉ−Ｍｏ系合金鋼等）からなる中空もしくは中実
形状の円柱体を基材とし、その外周を本発明の焼結合金
で被覆した積層構造とすることができる。[0024] The high-speed steel sintered alloy of the present invention has a wide variety of uses, but since wear resistance etc. are a matter of the surface of the member,
For example, when applying the sintered alloy of the present invention to the body of a rolling roll, an appropriate metal material (for example, JIS G
4105 Cr-Mo alloy steel, 4103 C
The laminated structure can be formed by using a hollow or solid cylindrical body made of (r-Ni-Mo alloy steel, etc.) as a base material and covering the outer periphery with the sintered alloy of the present invention.
【００２５】[0025]
【実施例】所定の化学組成に調整された高速度鋼系合金
粉末（平均粒径：２００μｍ）をカプセル材（軟鋼製）
に充填し、これに還元ガス（Ｈ２ガス）を導入して粉末
表面の酸化皮膜を還元除去処理（８００℃×２Ｈｒ）し
、脱気・密封したうえ、ＨＩＰ処理を行った。処理後、
カプセル材を機械加工により除去し、焼入れ・焼もどし
処理を行って供試焼結合金ブロックを得た。なお、焼入
れ処理は、真空チャバン内で、１１５０〜１２００℃に
、２Ｈｒ保持後、Ｎ２ガス（常温・常圧）を導入するガ
ス冷却により行い、焼もどし処理は、５４０〜５６０℃
に５〜１０Ｈｒ加熱保持して放冷するヒートパターンを
３回反復することにより行った。表１に供試焼結合金の
化学組成、表２に合金の融点と焼結処理条件を示す。Ｎ
ｏ．１〜８は、粗粒炭化物（粒径１０〜５０μｍ）を晶
出形成させた発明例であり、Ｎｏ．１０１〜１０４は、
粗粒炭化物の晶出形成の殆どない通常の焼結条件により
焼結された比較例である。図１は発明例Ｎｏ．２、図２
は比較例Ｎｏ．１０３のそれぞれの焼結合金の組織（走
査型電子顕微鏡写真、倍率１５００）を示している。比
較例Ｎｏ．１０３の炭化物の平均粒径は約２μｍである
。[Example] High-speed steel alloy powder (average particle size: 200 μm) adjusted to a predetermined chemical composition is used as a capsule material (made of mild steel)
A reducing gas (H2 gas) was introduced into the powder to remove the oxide film on the surface of the powder (800° C. x 2 hours), and the powder was degassed and sealed, followed by HIP treatment. After treatment,
The capsule material was removed by machining, and a test sintered alloy block was obtained by quenching and tempering. The quenching process is performed in a vacuum chamber at 1150 to 1200°C for 2 hours, followed by gas cooling by introducing N2 gas (normal temperature, normal pressure), and the tempering process is performed at 540 to 560°C.
This was done by repeating a heat pattern of heating and holding for 5 to 10 hours and allowing to cool three times. Table 1 shows the chemical composition of the test sintered alloy, and Table 2 shows the melting point and sintering conditions of the alloy. N
o. Nos. 1 to 8 are invention examples in which coarse grained carbide (particle size: 10 to 50 μm) was crystallized; 101 to 104 are
This is a comparative example sintered under normal sintering conditions with almost no crystallization of coarse carbides. FIG. 1 shows invention example No. 2.Figure 2
is comparative example No. 103 shows the structure of each sintered alloy (scanning electron micrograph, magnification: 1500). Comparative example no. The average grain size of the carbide of No. 103 is about 2 μm.
【００２６】表３は各供試焼結合金について、基地中の
粗粒炭化物（１０〜５０μｍ）の面積率、および諸特性
試験結果を示している。Table 3 shows the area ratio of coarse carbides (10 to 50 μm) in the matrix and the results of various characteristic tests for each of the sintered alloys tested.
【００２７】（１）摩耗試験
大越式迅速摩耗試験により比摩耗量（ｍｍ２／ｋｇｆ）
を測定
（ｉ） 回転輪：ＳＵＪ２：硬度（ＨＲＣ）６０、回
転輪幅３．０ｍｍ
（ｉｉ） 摩耗速度：３．４ｍ／ｓｅｃ （ｉｉｉ
）摩耗距離：２００ｍ
（ＩＶ） 最終荷重：１６．８Ｋｇ・ｆ（２）曲げ試
験
３点曲げ法により曲げ強さ（ｋｇｆ／ｍｍ２）を測定。
試験片サイズ：３×４×５０，ｍｍ、スパン距離：３０
ｍｍ。
（３）靭性試験
ヌープ圧子圧痕法により破壊靭性値ＫＩＣ（ＭＮｍ３／
２）を測定。(1) Wear test The specific wear amount (mm2/kgf) was determined by the Okoshi type rapid wear test.
Measure (i) Rotating wheel: SUJ2: hardness (HRC) 60, rotating wheel width 3.0 mm (ii) Wear rate: 3.4 m/sec (iii
) Wear distance: 200 m (IV) Final load: 16.8 Kg・f (2) Bending test Measure bending strength (kgf/mm2) using the 3-point bending method. Test piece size: 3 x 4 x 50, mm, span distance: 30
mm. (3) Toughness test Fracture toughness value KIC (MNm3/
Measure 2).
【００２８】[0028]
【表１】[Table 1]
【００２９】[0029]
【表２】[Table 2]
【００３０】[0030]
【表３】[Table 3]
【００３１】表３に示したように、発明例Ｎｏ．１〜８
の焼結合金は高硬度・高耐摩耗性を有していると同時に
、曲げ強度が高く、かつ破壊靭性値もすぐれている。
この改良された曲げ強度や破壊靭性値は、粗粒炭化物に
よるクラック伝播の抵抗性改善効果によるものであり、
粗粒炭化物を殆ど含まない比較例Ｎｏ．１０１〜１０４
との差異は歴然である。As shown in Table 3, invention example No. 1-8
The sintered alloy has high hardness and high wear resistance, as well as high bending strength and excellent fracture toughness. This improved bending strength and fracture toughness is due to the improved crack propagation resistance effect of coarse carbides.
Comparative example No. containing almost no coarse carbide. 101-104
The difference is obvious.
【００３２】[0032]
【発明の効果】本発明の高速度鋼系焼結合金は、硬質・
高耐摩耗性と併せて、クラック伝播の抵抗性にすぐれ、
高靭性を備えている。従って、圧延用ロール等、曲げ荷
重や、熱的・機械的衝撃等が作用する摩耗用途の部材料
として有用である。[Effect of the invention] The high-speed steel sintered alloy of the present invention is hard and
In addition to high wear resistance, it also has excellent crack propagation resistance.
It has high toughness. Therefore, it is useful as a part material for wear applications such as rolling rolls, which are subjected to bending loads, thermal and mechanical shocks, and the like.
【図１】本発明の焼結合金の金属組織を示す図面代用顕
微鏡写真[Fig. 1] Microscopic photograph used as a drawing showing the metal structure of the sintered alloy of the present invention
【図２】焼結合金（比較材）の金属組織を示す図面代用
顕微鏡写真[Figure 2] Microscopic photograph used as a drawing showing the metal structure of a sintered alloy (comparative material)
Claims (3)
％以下、Ｍｎ：０．４％以下，Ｃｒ：３〜２０％，Ｖ，
Ｔｉ，Ｎｂのいずれか１種ないし２種以上の元素：１２
％以下，Ｗ：５〜１４％，Ｍｏ：３〜９％，Ｃｏ：７〜
１４％，残部実質的にＦｅからなり、基地中に、粒径１
０〜５０μｍの炭化物粒が均一に分散し、その面積率は
１０〜５０％であることを特徴とする耐摩耗性・靭性等
にすぐれた高速度鋼系焼結合金。[Claim 1] C: 1.7-3.5%, Si: 0.4
% or less, Mn: 0.4% or less, Cr: 3 to 20%, V,
One or more elements of Ti and Nb: 12
% or less, W: 5-14%, Mo: 3-9%, Co: 7-
14%, the remainder essentially consists of Fe, with grain size 1
A high-speed steel-based sintered alloy with excellent wear resistance, toughness, etc., characterized by uniformly dispersed carbide grains of 0 to 50 μm and an area ratio of 10 to 50%.
〜３．５％、Ｍｎ：０．４％以下，Ｃｒ：３〜２０％，
Ｖ，Ｔｉ，Ｎｂのいずれか１種ないし２種以上の元素：
１２％以下，Ｗ：５〜１４％，Ｍｏ：３〜９％，Ｃｏ：
７〜１４％，残部実質的にＦｅからなり、基地中に、粒
径１０〜５０μｍの炭化物粒が均一に分散し、その面積
率は１０〜５０％であることを特徴とする耐摩耗性・靭
性等にすぐれた高速度鋼系焼結合金。[Claim 2] C: 1.7 to 3.5%, Si: 0.6
~3.5%, Mn: 0.4% or less, Cr: 3-20%,
One or more elements of V, Ti, and Nb:
12% or less, W: 5-14%, Mo: 3-9%, Co:
7 to 14%, the remainder substantially consisting of Fe, and carbide grains with a grain size of 10 to 50 μm are uniformly dispersed in the matrix, and the area ratio is 10 to 50%. A high-speed steel-based sintered alloy with excellent toughness.
または２種を含有する請求項１または請求項２に記載の
耐摩耗性・靭性等にすぐれた高速度鋼系焼結合金。3. The high-speed steel sintered bond with excellent wear resistance, toughness, etc. according to claim 1 or 2, which contains one or both of B: 2% or less and Ni: 3% or less. Money.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP14700991A JP2857724B2 (en) | 1991-04-01 | 1991-04-01 | High speed steel based sintered alloy |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP14700991A JP2857724B2 (en) | 1991-04-01 | 1991-04-01 | High speed steel based sintered alloy |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH04358046A true JPH04358046A (en) | 1992-12-11 |
| JP2857724B2 JP2857724B2 (en) | 1999-02-17 |
Family
ID=15420494
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP14700991A Expired - Lifetime JP2857724B2 (en) | 1991-04-01 | 1991-04-01 | High speed steel based sintered alloy |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP2857724B2 (en) |
Cited By (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH05148510A (en) * | 1991-04-22 | 1993-06-15 | Hitachi Metals Ltd | Wear resistant composite roll and manufacture thereof |
| FR2722211A1 (en) * | 1994-07-06 | 1996-01-12 | Thyssen Aciers Speciaux Sa | Wear-resistant tool steel |
| US20150284829A1 (en) * | 2014-04-07 | 2015-10-08 | Scoperta, Inc. | Fine-grained high carbide cast iron alloys |
| US20160289803A1 (en) * | 2015-04-06 | 2016-10-06 | Scoperta, Inc. | Fine-grained high carbide cast iron alloys |
| US10173290B2 (en) | 2014-06-09 | 2019-01-08 | Scoperta, Inc. | Crack resistant hardfacing alloys |
| US10329647B2 (en) | 2014-12-16 | 2019-06-25 | Scoperta, Inc. | Tough and wear resistant ferrous alloys containing multiple hardphases |
| US11085102B2 (en) | 2011-12-30 | 2021-08-10 | Oerlikon Metco (Us) Inc. | Coating compositions |
| US11253957B2 (en) | 2015-09-04 | 2022-02-22 | Oerlikon Metco (Us) Inc. | Chromium free and low-chromium wear resistant alloys |
| US11939646B2 (en) | 2018-10-26 | 2024-03-26 | Oerlikon Metco (Us) Inc. | Corrosion and wear resistant nickel based alloys |
-
1991
- 1991-04-01 JP JP14700991A patent/JP2857724B2/en not_active Expired - Lifetime
Cited By (11)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH05148510A (en) * | 1991-04-22 | 1993-06-15 | Hitachi Metals Ltd | Wear resistant composite roll and manufacture thereof |
| FR2722211A1 (en) * | 1994-07-06 | 1996-01-12 | Thyssen Aciers Speciaux Sa | Wear-resistant tool steel |
| US11085102B2 (en) | 2011-12-30 | 2021-08-10 | Oerlikon Metco (Us) Inc. | Coating compositions |
| US20150284829A1 (en) * | 2014-04-07 | 2015-10-08 | Scoperta, Inc. | Fine-grained high carbide cast iron alloys |
| US10173290B2 (en) | 2014-06-09 | 2019-01-08 | Scoperta, Inc. | Crack resistant hardfacing alloys |
| US11111912B2 (en) | 2014-06-09 | 2021-09-07 | Oerlikon Metco (Us) Inc. | Crack resistant hardfacing alloys |
| US11130205B2 (en) | 2014-06-09 | 2021-09-28 | Oerlikon Metco (Us) Inc. | Crack resistant hardfacing alloys |
| US10329647B2 (en) | 2014-12-16 | 2019-06-25 | Scoperta, Inc. | Tough and wear resistant ferrous alloys containing multiple hardphases |
| US20160289803A1 (en) * | 2015-04-06 | 2016-10-06 | Scoperta, Inc. | Fine-grained high carbide cast iron alloys |
| US11253957B2 (en) | 2015-09-04 | 2022-02-22 | Oerlikon Metco (Us) Inc. | Chromium free and low-chromium wear resistant alloys |
| US11939646B2 (en) | 2018-10-26 | 2024-03-26 | Oerlikon Metco (Us) Inc. | Corrosion and wear resistant nickel based alloys |
Also Published As
| Publication number | Publication date |
|---|---|
| JP2857724B2 (en) | 1999-02-17 |
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