JPH0499157A - Sintered alloy steel excellent in wear resistance and toughness - Google Patents
Sintered alloy steel excellent in wear resistance and toughnessInfo
- Publication number
- JPH0499157A JPH0499157A JP20855990A JP20855990A JPH0499157A JP H0499157 A JPH0499157 A JP H0499157A JP 20855990 A JP20855990 A JP 20855990A JP 20855990 A JP20855990 A JP 20855990A JP H0499157 A JPH0499157 A JP H0499157A
- Authority
- JP
- Japan
- Prior art keywords
- alloy steel
- toughness
- sintered alloy
- wear resistance
- carbides
- 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.)
- Pending
Links
- 229910000851 Alloy steel Inorganic materials 0.000 title claims abstract description 21
- 150000001247 metal acetylides Chemical class 0.000 claims abstract description 22
- 229910052721 tungsten Inorganic materials 0.000 claims abstract description 14
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 13
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 11
- 229910000734 martensite Inorganic materials 0.000 claims abstract description 7
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 7
- 229910052715 tantalum Inorganic materials 0.000 claims abstract description 6
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 6
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 4
- 239000010936 titanium Substances 0.000 claims description 6
- 239000012535 impurity Substances 0.000 claims description 4
- NRTOMJZYCJJWKI-UHFFFAOYSA-N Titanium nitride Chemical compound [Ti]#N NRTOMJZYCJJWKI-UHFFFAOYSA-N 0.000 claims description 3
- 229910052742 iron Inorganic materials 0.000 claims description 2
- 239000000843 powder Substances 0.000 abstract description 25
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 abstract description 15
- 239000000203 mixture Substances 0.000 abstract description 13
- 239000011159 matrix material Substances 0.000 abstract description 7
- 229910044991 metal oxide Inorganic materials 0.000 abstract description 4
- 150000004706 metal oxides Chemical class 0.000 abstract description 4
- 238000000034 method Methods 0.000 abstract description 3
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 abstract description 2
- 238000005496 tempering Methods 0.000 abstract description 2
- 238000001513 hot isostatic pressing Methods 0.000 abstract 2
- 229910052799 carbon Inorganic materials 0.000 abstract 1
- 229910002804 graphite Inorganic materials 0.000 abstract 1
- 239000010439 graphite Substances 0.000 abstract 1
- 239000002184 metal Substances 0.000 abstract 1
- 229910052751 metal Inorganic materials 0.000 abstract 1
- 229910000831 Steel Inorganic materials 0.000 description 16
- 239000010959 steel Substances 0.000 description 16
- 230000000694 effects Effects 0.000 description 9
- 229910045601 alloy Inorganic materials 0.000 description 7
- 239000000956 alloy Substances 0.000 description 7
- 239000000463 material Substances 0.000 description 6
- 230000007423 decrease Effects 0.000 description 3
- 239000006104 solid solution Substances 0.000 description 3
- 238000005520 cutting process Methods 0.000 description 2
- 239000002245 particle Substances 0.000 description 2
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 1
- 238000002441 X-ray diffraction Methods 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- 239000003610 charcoal Substances 0.000 description 1
- 238000005097 cold rolling Methods 0.000 description 1
- 239000000470 constituent Substances 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- PCHJSUWPFVWCPO-UHFFFAOYSA-N gold Chemical compound [Au] PCHJSUWPFVWCPO-UHFFFAOYSA-N 0.000 description 1
- 239000010931 gold Substances 0.000 description 1
- 229910052737 gold Inorganic materials 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
- 239000004615 ingredient Substances 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
- 239000011812 mixed powder Substances 0.000 description 1
- 238000004663 powder metallurgy Methods 0.000 description 1
- 238000010298 pulverizing process Methods 0.000 description 1
- 238000010791 quenching Methods 0.000 description 1
- 230000000171 quenching effect Effects 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 238000002310 reflectometry Methods 0.000 description 1
- 238000005096 rolling process Methods 0.000 description 1
- 150000003839 salts Chemical class 0.000 description 1
- 239000000758 substrate Substances 0.000 description 1
Landscapes
- Powder Metallurgy (AREA)
Abstract
Description
【発明の詳細な説明】
〔産業上の利用分野〕
この発明は、素地に分散する炭化物の主体を微細にして
硬質のＭＣ型炭化物で構成することによりすぐれた耐摩
耗性と靭性を具備せしめた焼結合金鋼に関するものであ
る。[Detailed Description of the Invention] [Industrial Application Field] This invention provides excellent wear resistance and toughness by making the carbide dispersed in the matrix fine and composed of hard MC type carbide. This relates to sintered alloy steel.
従来、例えば特公昭５７−５５７８２号公報や特開昭５
８−１８１８４８号公報などに記載されるように、重量
？０で（以下Ｏｏは重量％を示す）、
Ｃ： ｌ 、 ５〜４ 、５％、 Ｃｒ：２〜６
％、Ｗ： ０．５〜ＩＯ％、 Ｍｏ ： ５〜
１５％、ｖ ： ３〜ｔｏ９ｏ、 Ｔｌ
： ２〜１２％、Ｎ ： ０．３〜３ 、５％、
を含有し、さらに必要に応じて１
１．ρＪｉｊ、ζｒ １〜１５％、
を含有し、残りがＦｅと不１−ＩＪ避不純物からなる組
成、
並びに、焼戻しマルテンサイトを主体とした素地に、炭
化物と窒化チタン（以下ＴｉＮで示す）が分散した組織
、
をａする焼結合金鋼が知られており、さらにこれら焼結
合金鋼か、熱間および冷間圧延ロールや転造ダイスなど
の耐摩工具や、各種切削工具などとして用いられている
ことも良く知られるところである。Conventionally, for example, Japanese Patent Publication No. 57-55782 and Japanese Unexamined Patent Publication No. 5
As stated in Publication No. 8-181848 etc., weight 0 (hereinafter Oo indicates weight%), C: l, 5-4, 5%, Cr: 2-6
%, W: 0.5~IO%, Mo: 5~
15%, v: 3~to9o, Tl
: 2 to 12%, N: 0.3 to 3.5%, and further 11. as necessary. ρJij, ζr 1 to 15%, with the remainder consisting of Fe and impurities avoided by IJ, and carbide and titanium nitride (hereinafter referred to as TiN) are dispersed in a matrix mainly composed of tempered martensite. Sintered alloy steels with a microstructure, a, are known, and these sintered alloy steels are used in wear-resistant tools such as hot and cold rolling rolls and rolling dies, as well as various cutting tools. This is also well known.
一方、上記の従来焼結合金鋼においては、素地に分散す
る炭化物がＭＣ型以外に、Ｍ６Ｃ。On the other hand, in the above-mentioned conventional sintered alloy steel, the carbides dispersed in the matrix are not only MC type but also M6C type.
ＭＣおよびＭ２Ｃ型などの多数の形態の炭２３６ 。Charcoal 236 in numerous forms such as MC and M2C types.
化物で構成されており、一般にＭＣ型炭化物以外は映さ
が低く、かつ粗大化し易いために、十分な耐摩耗性を得
ることができず、靭性の而でも満足する結果を示さない
のが現状である。In general, carbides other than MC-type carbide have low reflectivity and tend to coarsen, making it impossible to obtain sufficient wear resistance and not showing satisfactory results in terms of toughness. be.
そこで、本発明者等は、上述のような観点から、上記の
焼結合金鋼の素地に分散する炭化物に着［１し研究をｊ
Ｔなった結果、
上記従来焼結合金鋼に合金成分としてＮｂおよびＴａの
うちの１種または２種を２〜１０％の割合で含Ｈさせる
と、素地中に分散する炭化物は、その主体がＭＣ型とな
り、かつ平均粒径で０．５〜５〜と微細化し、したがっ
てこの結果の焼結合金鋼はすぐれた耐Ｙ粍性と靭性を具
備するようになるという研究結果を得たのである。Therefore, from the above-mentioned viewpoint, the present inventors conducted research on carbides dispersed in the matrix of the above-mentioned sintered alloy steel.
As a result, when one or two of Nb and Ta are added as alloying ingredients to the conventional sintered alloy steel at a ratio of 2 to 10%, the carbides dispersed in the base material are mainly The research results showed that the sintered alloy steel had an MC type and was refined to an average grain size of 0.5 to 5. Therefore, the resulting sintered alloy steel had excellent Y corrosion resistance and toughness. .
この発明は、上記研究結果にもとづいてなされたしので
あって、
Ｃ：１．５〜４．５％、 Ｃｒ：２〜６％、Ｗ
： ０．５〜１０°６、 Ｍｏ ： ５〜１５
％、■＝３〜ＩＯ？０１ ＴＩ ：２〜１２
％、Ｎ ： ０．３〜３ 、５％、
ＮｂおよびＴａのうちの１ｆ１！または２種：２〜ｌｏ
％、を含有し、さらに必要に応じて、
Ｃｏ ： １〜１５’６、
を含有し、残りがＦ（３と不ｎ〕避不純物からなる組成
、
並びに、焼戻しマルテンサイトを主体とした素地に、甲
均粒径二〇、５〜５μｓのＭＣ型炭化物を主体とする炭
化物とＴｉＮが均一に分散した組織、を白°する耐摩耗
性および靭性のすぐれた焼結合金鋼に特徴を白゛するも
のである。This invention was made based on the above research results, and includes: C: 1.5 to 4.5%, Cr: 2 to 6%, W
: 0.5~10°6, Mo: 5~15
%,■=3~IO? 01 TI: 2-12
%, N: 0.3-3, 5%, 1f1 of Nb and Ta! Or 2 types: 2~lo
%, and if necessary, Co: 1 to 15'6, with the remainder being F (3 and non) impurities, and a base material mainly composed of tempered martensite. , A sintered alloy steel with excellent wear resistance and toughness, which has a structure in which TiN and carbides mainly composed of MC type carbides with an average grain size of 20, 5 to 5 μs are uniformly dispersed. It is something to do.
つぎに、この発明の焼結合金鋼において、成分組成を上
記の通りに限定した理由を説明する。Next, the reason why the composition of the sintered alloy steel of the present invention is limited as described above will be explained.
（ａ） Ｃ
Ｃ成分には、素地に固溶して、これの硬さおよび強攻を
向上させるほか、Ｃｒ 、Ｗ、ＭｏおよびＶ、さらにＮ
ｂ、Ｔａと結合して炭化物を形成し、鋼の耐摩耗性を向
上させる作用があるが、その含有量が１°６未満では前
記作用に所望の効果がｉりらレス、−ｈ゛この含有量が
４．５％を越えると鋼の靭性が０（ドするようになるこ
とから、その含有量を１．５〜４ 、５９ｏと定めた。(a) C The C component includes Cr, W, Mo, and V, as well as N, which improves the hardness and toughness of the substrate by forming a solid solution therein.
b. It combines with Ta to form carbides, which has the effect of improving the wear resistance of steel, but if its content is less than 1°6, the desired effect is not achieved, -h. If the amount exceeds 4.5%, the toughness of the steel becomes zero, so the content was determined to be 1.5 to 4.59°.
（ｂ） Ｃｒ 、 Ｗ、 Ｍｏ 、および■これらの
成分には、いずれもその一部が素地に開演してこれを強
化するほか、上記の通りＣと結合して炭化物を形成し、
鋼の耐摩耗性を向上させる作ＪＴＩがあるが、その金白
゛息がＣｒ 、 Ｗ、 Ｍｏ 。(b) Cr, W, Mo, and ■ In each of these components, some of them open to the base material and strengthen it, and as mentioned above, combine with C to form carbide,
There is a product called JTI that improves the wear resistance of steel, but its gold white is made of Cr, W, and Mo.
およびＶのうちのいずれかでも、それぞれＣｒ：２％未
満、Ｗ：０．５％未満、Ｍｏ：５％未満、およびＶ：３
％未満になると前記作用に所望の効果が得られず、一方
Ｃｒ 、 Ｗ、 Ｍ□ 、およびＶのうちのいずれかの
含Ｈ量でも、それぞれＣｒ：６％、Ｗ：ｌＱ％、Ｍｏ：
Ｉ５’ｏ、およびＶ ： １０％を越えると、炭化物生
酸量が多くなりすぎて鋼の靭性が低下するようになるこ
とから、そのａ Ｈｍを、それぞれＣ「：２〜６％、Ｗ
： ０．５〜ＩＯ％、Ｍｏ： ５〜１５％、オヨびＶ
：３〜１０？６と定めた。and V, respectively Cr: less than 2%, W: less than 0.5%, Mo: less than 5%, and V: 3
%, the desired effect cannot be obtained in the above action, and on the other hand, even if the H content of any one of Cr, W, M□, and V is Cr: 6%, W: lQ%, Mo:
I5'o and V: If it exceeds 10%, the amount of carbide bioacid becomes too large and the toughness of the steel decreases.
: 0.5~IO%, Mo: 5~15%, Oyobi V
:3 to 10?6.
（ｃ）ＴｉおよびＮ
これら２成分は、主体が素地に分散するＴｉＮを構成す
るものであり、このＴｉＮの分散含有によって鋼の耐摩
耗性、被加工材との耐溶亡性、および耐熱性か向上する
ようになるか、その含有量かそれぞれＴｉ：２％未満お
よびＮ ： ０．３％未満ては、分散相としてのＴｉＮ
の割合が少なすぎて前記作用に所望の効果か得られず、
一方その含有量がＴｉ：Ｉ２００およびＮ ： ３．５
％を越えると、ＴｉＮの割合が多くなりすぎて鋼の靭性
が低下するようになることから、これら成分の含有量を
、Ｔｉ：２〜１２０ｏ、 Ｎ ： ０．３〜３．５％と
定めた。(c) Ti and N These two components mainly constitute TiN dispersed in the base material, and the dispersed content of TiN improves the wear resistance of the steel, the melting resistance with the workpiece, and the heat resistance. The content of Ti: less than 2% and N: less than 0.3%, respectively, increases with TiN as a dispersed phase.
The proportion of is too small to achieve the desired effect,
On the other hand, the content is Ti:I200 and N: 3.5
%, the proportion of TiN becomes too large and the toughness of the steel decreases. Therefore, the contents of these components are set as Ti: 2 to 120% and N: 0.3 to 3.5%. Ta.
（ｄ）Ｎｂ、Ｔａ
これらの成分には、Ｃｒ 、Ｗ、Ｍｏ 、および■と同
様に素地に固溶して、これを強化すると共に、Ｃｒ 、
Ｗ、Ｍｏ 、および■と微細な固溶体炭化物を形成して
、その形態を硬質のＭＣ型にする作用があり、この結果
として鋼はすぐれた耐摩耗性と靭性を具備するようにな
るが、その含有量が２％未満では前記作用に所望の効果
が得られず、一方その含有量か１０％を越えても鋼には
靭性に低下傾向か現われるようになることから、その含
有量を２〜１０％と定めた。(d) Nb, Ta These components include Cr, W, Mo, and solid solution in the base material to strengthen it, as well as Cr, W, Mo, and
Forms fine solid solution carbides with W, Mo, and If the content is less than 2%, the desired effect cannot be obtained, while if the content exceeds 10%, the steel will tend to decrease in toughness. It was set at 10%.
（ｃ） Ｃ。(c) C.
Ｃｏ成分には、素地に固溶して、鋼の耐熱性を向上させ
る効果があるので必要に応じて含有させるが、その含有
量が１％未満では所望の耐熱性向上効果が得られず、一
方その含有量が１５％を越えてもより一層の向上効果は
現われずト経済性を考慮して、その含６ｍを１〜１５％
と定めた。The Co component is dissolved in the base material and has the effect of improving the heat resistance of steel, so it is included as necessary, but if the content is less than 1%, the desired effect of improving heat resistance cannot be obtained. On the other hand, even if the content exceeds 15%, further improvement effects will not appear, and in consideration of economic efficiency, the content should be reduced to 1 to 15%.
It was determined that
なお、この発明の焼結合金鋼は、通常の粉末冶金法にて
、原料粉末として、Ｃ粉末、Ｃ「粉末、Ｗ粉末、Ｍｏ粉
末、■粉末、Ｎｂ粉末、およびＴａ粉末、並びにこれら
の炭化物粉末のうちの所要粉末と、Ｃｏ粉末の要素粉末
とＴｉＮ粉末を用い、これらを所定の組成で混合するか
、あるいは所定組成の合金鋼粉末にＴｉＮ粉末と混合す
るか、さらにＴｉＮ粉末を除く、構成成分の酸化物粉末
を用い、まず、所定組成の合金鋼に対応した組成に、こ
れら金属酸化物粉末を配合し、還元用Ｃ粉末を加えた状
態で、水素雰囲気中で共還元処理を施し、これにＴｉＮ
粉末と、必要に応じて上記要素粉末の１種以上を加えて
成分調整して、混合するかしくこの場合、ＴｉＮ粉末を
最初から金属酸化物粉末と混合した状態で加えておき、
これに共還元処理を施してもよい）、ついで圧粉体にプ
レス成形し、これを通常の条件で焼結することによって
製造されるものである。Incidentally, the sintered alloy steel of the present invention is produced by using a normal powder metallurgy method as raw material powders such as C powder, C powder, W powder, Mo powder, ■ powder, Nb powder, Ta powder, and carbides thereof. Using the required powder of the powders, elemental powder of Co powder, and TiN powder, mixing these in a predetermined composition, or mixing alloy steel powder with a predetermined composition with TiN powder, and further excluding the TiN powder, Using the constituent oxide powders, first, these metal oxide powders are blended into a composition corresponding to alloy steel of a predetermined composition, and with the addition of C powder for reduction, co-reduction treatment is performed in a hydrogen atmosphere. , and TiN
If necessary, add the TiN powder and one or more of the above elemental powders to adjust the composition and mix.In this case, add the TiN powder mixed with the metal oxide powder from the beginning.
This may be subjected to co-reduction treatment), then press-molded into a green compact, and sintered under normal conditions.
つぎに、この発明の焼結合金鋼を実施例により具体的に
説明する。Next, the sintered alloy steel of the present invention will be specifically explained with reference to Examples.
まず、上記の共還元法にて、所定の割合に配合した金属
酸化物粉末と黒鉛粉末（Ｃ粉末）の混合粉末から、それ
ぞれ第１表に示される組成、並びに軽い粉砕を加えて平
均粒径を１〜２ｍとした合金鋼粉末を調製し、これに平
均粒径二２ｐのＴｉＮ粉末および必要に応じて構成成分
粉末を同しく第１表に示される割合で配合し、ボールミ
ルで混合した後、６ｉｏｎ／ｃｄの圧力で圧粉体にプレ
ス成形し、この圧粉体を、真空中、１２００〜１２５０
℃の温度で焼結し、ついで得られた焼結体に、Ａ「雰囲
気中、圧カニ １０００気圧、温度： １２００〜１２
５０℃の条件てＨＩＰ処理を施した後、１２００℃から
塩浴中に焼入れし、引続いて温度：５６０℃で３回の焼
戻し処理を施すことにより本発明焼結合金鋼１〜９およ
び従来焼結合金鋼１〜２をそれぞれ製造した。First, by using the co-reduction method described above, a mixed powder of metal oxide powder and graphite powder (C powder) blended in a predetermined ratio is obtained, and the composition shown in Table 1 and the average particle size are obtained by light pulverization. Prepare alloy steel powder with a diameter of 1 to 2 m, and add TiN powder with an average particle size of 22p and component powder as necessary in the proportions shown in Table 1, and mix in a ball mill. , 6 ion/cd into a green compact, and the green compact is heated to a temperature of 1200 to 1250 in a vacuum.
The resulting sintered body was sintered at a temperature of 1,200 to 12 °C in an atmosphere of A pressure crab at 1,000 atm, temperature: 1,200 to 12
After HIPing at 50°C, quenching in a salt bath from 1200°C, followed by tempering three times at 560°C, the sintered alloy steels 1 to 9 of the present invention and the conventional Sintered alloy steels 1 and 2 were manufactured, respectively.
ついで、この結果得られた各種の焼結合金鋼について、
組織観察とＸ線回折により炭化物の平均粒径と、炭化物
に占めるＭＣ型炭化物の割合を測定すると共に、成分組
成を測定し、さらに耐摩耗性と靭性を評価する目的でロ
ックウェル硬さ（Ｃスケール）と抗折力を測定した。こ
れらの測定結果を第２表に示した。Next, regarding the various sintered alloy steels obtained as a result,
In addition to measuring the average grain size of carbides and the proportion of MC type carbides in the carbides by microstructural observation and X-ray diffraction, we also measured the component composition, and also measured the Rockwell hardness (C) for the purpose of evaluating wear resistance and toughness. scale) and transverse rupture strength were measured. The results of these measurements are shown in Table 2.
第２表に示される結果から、本発明焼結合金鋼１〜９は
、いずれもＮｂおよび／またはＴａの含Ｈによって焼戻
しマルテンサイトを主体とする素地中に分散する炭化物
が微細で、かつ炭化物の主体がＭＣ型で占められており
、この結果高硬度と高靭性を示すのに対して、従来焼結
合金鋼１〜２は、いずれも素地の焼戻しマルテンサイト
中に分散する炭化物の粒径が相対的に大きく、炭化物の
主体かＭＣ型以外のＭ ＣやＭ２３Ｃ６、さらにＭ２
Ｃ型などからなり、したかって硬さおよび靭性とも相χ
・Ｉ的に低いことか明らかである。From the results shown in Table 2, all of the sintered alloy steels 1 to 9 of the present invention have fine carbides dispersed in the matrix mainly composed of tempered martensite due to the H content of Nb and/or Ta. The main body of the steel is the MC type, which shows high hardness and high toughness, whereas conventional sintered alloy steels 1 and 2 have a grain size of carbides dispersed in the tempered martensite base. is relatively large, and is mainly composed of carbides or other types other than MC, such as MC, M23C6, and even M2.
C type, etc., and therefore the hardness and toughness are also inconsistent.
・It is clear that the I level is low.
上述のように、この発明の焼結合金鋼は、特に炭化物が
均一微細で、かつその主体が硬質のＭＣ型で占められて
いるので、硬さおよび靭性ともすくれたものになってお
り、したがって各種の耐摩工具や切削工具などの製造に
適用した場合に長期に亘ってすぐれた性能を発揮するの
である。As mentioned above, the sintered alloy steel of the present invention has uniformly fine carbides and is mainly composed of hard MC type, so it has poor hardness and toughness. It exhibits excellent performance over a long period of time when applied to the manufacture of various wear-resistant tools and cutting tools.
Claims (2)
．５〜１０％、Ｍｏ：５〜１５％、 Ｖ：３〜１０％、Ｔｉ：２〜１２％、 Ｎ：０．３〜３．５％、 ＮｂおよびＴａのうちの１種または２種： ２〜１０％、 を含有し、残りがＦｅと不可避不純物からなる組成（以
上重量％）、並びに、 焼戻しマルテンサイトを主体とした素地に、平均粒径：
０．５〜５μｍのＭＣ型炭化物を主体とする炭化物と窒
化チタンが均一に分散した組織、を有することを特徴と
する耐摩耗性および靭性のすぐれた焼結合金鋼。(1) C: 1.5-4.5%, Cr: 2-6%, W: 0
．． 5-10%, Mo: 5-15%, V: 3-10%, Ti: 2-12%, N: 0.3-3.5%, one or two of Nb and Ta: 2 ~10%, with the remainder consisting of Fe and unavoidable impurities (wt%), and a base mainly composed of tempered martensite, with an average grain size:
A sintered alloy steel with excellent wear resistance and toughness, characterized by having a structure in which carbides mainly consisting of 0.5 to 5 μm MC type carbides and titanium nitride are uniformly dispersed.
．５〜１０％、Ｍｏ：５〜１５％、 Ｖ：３〜１０％、Ｔｉ：２〜１２％、 Ｎ：０．３〜３．５％、 ＮｂおよびＴａのうちの１種または２種： ２〜１０％、 を含有し、さらに、 Ｃｏ：１〜１５％、 を含有し、残りがＦｅと不可避不純物からなる組成（以
上重量％）、並びに、 焼戻しマルテンサイトを主体とした素地に、平均粒径：
０．５〜５μｍのＭＣ型炭化物を主体とする炭化物と窒
化チタンが均一に分散した組織、を有することを特徴と
する耐摩耗性および靭性のすぐれた焼結合金鋼。(2) C: 1.5-4.5%, Cr: 2-6%, W: 0
．． 5-10%, Mo: 5-15%, V: 3-10%, Ti: 2-12%, N: 0.3-3.5%, one or two of Nb and Ta: 2 ~10%, and further contains Co: 1~15%, with the remainder being Fe and unavoidable impurities (weight%), and an average grain size on a base mainly composed of tempered martensite. Diameter:
A sintered alloy steel with excellent wear resistance and toughness, characterized by having a structure in which carbides mainly consisting of 0.5 to 5 μm MC type carbides and titanium nitride are uniformly dispersed.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP20855990A JPH0499157A (en) | 1990-08-07 | 1990-08-07 | Sintered alloy steel excellent in wear resistance and toughness |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP20855990A JPH0499157A (en) | 1990-08-07 | 1990-08-07 | Sintered alloy steel excellent in wear resistance and toughness |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH0499157A true JPH0499157A (en) | 1992-03-31 |
Family
ID=16558192
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP20855990A Pending JPH0499157A (en) | 1990-08-07 | 1990-08-07 | Sintered alloy steel excellent in wear resistance and toughness |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0499157A (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN105420629A (en) * | 2015-10-29 | 2016-03-23 | 重庆川深金属新材料股份有限公司 | High-plasticity roller ring made of hard materials and suitable for high-speed wire rod rolling and manufacturing method |
| CN113981331A (en) * | 2021-11-16 | 2022-01-28 | 山东瑞尔达科技集团股份有限公司 | Powder metallurgy high-speed steel material for cutter |
-
1990
- 1990-08-07 JP JP20855990A patent/JPH0499157A/en active Pending
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN105420629A (en) * | 2015-10-29 | 2016-03-23 | 重庆川深金属新材料股份有限公司 | High-plasticity roller ring made of hard materials and suitable for high-speed wire rod rolling and manufacturing method |
| CN113981331A (en) * | 2021-11-16 | 2022-01-28 | 山东瑞尔达科技集团股份有限公司 | Powder metallurgy high-speed steel material for cutter |
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