CN100469936C - High-performance low-alloy niobium-contained high-speed steel - Google Patents
High-performance low-alloy niobium-contained high-speed steel Download PDFInfo
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Abstract
The invention belongs to the high speed steel field, mainly applied to the steel for high speed cutting bit, screwtap, vertical milling cutter, etc, also applied to the steel for high load mould, high temperature wearable parts, etc, especially relating to a high-performance, low-alloy, Nb-containing high speed steel, and its chemical composition includes in weight percent(wt%): C 0.95-1.15wt%, Si 0.20-0.40wt%, W 3.5-5.5wt%, Mo 2.0-4.0wt%, Cr 3.0- 4.5wt%, V 0.80-1.5wt%, Nb 0.5-1.5wt%, Re 0.01-0.02wt%, N 0.04-0.10wt%, S=< 0.030wt%, P=< 0.030wt%, and Mn=< 0.40wt%, and the rest Fe and impurities. As compared with the existing techniques, it has advantages of low production cost, high yield, quality easy to control, easy for large scale production, meeting the application requirements for good secondary hardness and red hardness, impact toughness and bending strength.
Description
Technical field
The invention belongs to the rapid steel field, mainly be applicable to steel such as high speed cutting drill bit, screw tap, slotting cutter, also can be applicable to the wear-resisting spare part of being on active service under high-load mould, the hot conditions etc. and use steel, particularly a kind of high-performance low-alloy contains the Nb rapid steel.
Background technology
In the prior art, along with the development of machinery manufacturing industry, the performance and the Financial cost of rapid steel are had higher requirement.At present, the main universal rapid steel that use countries in the world is M2 (W6Mo5Cr4V2), and China mainly uses M2 and W9 (W9Mo3Cr4V) rapid steel.Contain valuable alloying elements such as a large amount of W, Mo, Cr, V in the rapid steel, and lumber recovery is low.In order to save valuable strategic alloying element W, Mo, V etc., various countries have carried out the research of low alloy high speed steel, foremost D950, the M52 of the U.S., the S3-3-2 of Germany and the W4Mo3Cr4VSi of China that Sweden is arranged.Though these steel grades have been saved alloying element, but its use properties is restricted, can only use as low-grade cutter (being mainly machine hacksaw blade, rolling drill bit, wood cutter etc.), because the content of alloying element is lower, when comparatively high temps quenches, the trend of grain growth is obvious, and red hardness is low, can not substitute M2 and W9 (W9Mo3Cr4V) rapid steel under the situation of high request slightly.
In addition, publication No. is that the PCT of W09302818A has announced a kind of rapid steel of producing with powder metallurgy process, and its chemical ingredients (weight %) is C 0.6-0.9%, Si 0-1.0%, Mn 0-1.0%, Cr 0-5%, Mo0-10%, Mo+W/2 should be 4 at least, V 0.7-2%, Co≤14%, Nb 0.7-1.5%, all the other are Fe and unavoidable impurities.This steel be used to the to have relatively high expectations toughness and the suitable instrument of hardness and intensity, functional, toughness especially.But in this invention design of chemical composition, carbon content is lower, under Nb, the common situation about existing of V alloy element, especially under the Nb content condition with higher, be easy to generate tempering secondary hardening deficiency, thereby in the rapid steel scope, use, easily produce the relatively poor situation of red hardness, reduce the work-ing life of cutter.In addition, the rapid steel complex manufacturing that adopts powder metallurgy process to produce, cost is very high, is not easy to scale operation; And still there is inevitable shortcoming in powder metallurgy process: the oxygen level height, and material internal has hole simultaneously, and quality is wayward.
Summary of the invention
The object of the present invention is to provide and a kind ofly have that production cost is low, high yield, system easy to control the quality, be easy to scale operation, satisfy good secondary hardness and red hardness simultaneously, the high-performance low-alloy of impelling strength and bending strength application demand contains the Nb rapid steel.
According to above-mentioned purpose, the present invention suitably reduces the noble metal content of alloying element W, Mo, V on the basis of M2 (W6Mo5Cr4V2) and W9 (W9Mo3Cr4V), add relatively cheap strong carbide forming element Nb, make the performance of this rapid steel reach the performance of the higher W9 of alloying element content, M2 rapid steel, satisfy the use properties of complex cutting tool, simultaneously, can be used for cold-work die, have good and economic and use prospect.
The technical scheme of the integral body that the present invention adopts is: carbide forming element W, Mo in the universal rapid steel of (1) reduction and the content of V; (2) add strong carbide forming element Nb, part substitutes V or W, forms a large amount of primary carbides, and crystal grain thinning, to improve the wear resistance of rapid steel; (3) add proper amount of rare-earth element (Re), crystal boundary is purified, improve the thermoplasticity of this steel, thereby improve the lumber recovery of steel, and forging to roll generation can realize hot-work the time, reduce production costs.
The concrete technical scheme of the present invention is: the concrete chemical ingredients of this alloy (weight %) is: C 0.95～1.15%, and Si 0.20～0.40%, and W 3.5～5.5%, Mo 2.0～4.0%, Cr 3.0～4.5%, and V 0.80～1.5%, and Nb 0.5～1.5%, Re 0.01～0.02%, N 0.04～0.10%, S≤0.030%, P≤0.030%, Mn≤0.40%, all the other are Fe and unavoidable impurities.
The effect of above-mentioned each element and proportioning are according to as follows:
C: carbon is carbide forming element in rapid steel, and its content reaches according to alloying element to be decided the requirement of processing performance and use properties, generally between 0.80～1.5%.Carbon content is the alloying element of finally wanting in the rapid steel, and the processing performance and the use properties of rapid steel had crucial influence.In higher strong carbide element nb, the low-alloy high-speed steel of V content, because the adding of Nb, formation is difficult to dissolved MC type carbide.Should with due regard to carry high-carbon content, in drawing process, separate out, improve age hardening effect in order to the carbide that forms more V.But carbon content is too high, and quenching overheating, burning susceptibility and residual austenite are had negative impact, and reduces toughness.Carbon content among the present invention is defined as 0.95～1.15% according to fixed than carbon rule.
Mn: add as reductor, content generally is controlled at≤and 0.40%.In addition, Mn/S 〉=20 in the control steel are beneficial to the forging that improves rapid steel, the thermoplasticity of rolling, and obviously reduce base material crackle and improve lumber recovery.
Si: add as deoxidant element, content generally is controlled at 0.20～0.40%.In low-alloy high-speed steel, generally acknowledged obviously favourable to secondary hardening and hot hardness, therefore, in most low-alloy high-speed steel, all add 0.5～1.3% Si content.But in containing the higher rapid steel of W, Si does not only have benefit to secondary hardening, and owing to promote the formation of thick primary carbide MC, toughness to steel is unfavorable, other negative impact of Si also has, and increases the decarburization susceptibility of steel, slightly reduces the temperature of secondary hardening peak value, promote of the formation of non-coherence M6C carbide in higher tempering temperature, unfavorable to red hardness more than 600 ℃.Therefore, strictness limits its content 0.20～0.40% in low-alloy high-speed steel of the present invention.
Re: rare earth element has deoxidation, desulfuration in steel, changes inclusion morphology, and crystal boundary is purified, refined cast structure, the effects such as high-temperature oxidation resistant non-scale that improve steel.Add a certain amount of rare earth element in rapid steel, it is about more than 10～60% to improve thermoplasticity, thereby improves the lumber recovery of steel, and forging to roll generation can realize hot-work the time, reduces production costs.Simultaneously, the adding of rare earth alloy element, the processing of can going bad to thick carbide.Because rare earth is very active element, it is improper or too much to add, and can increase the non-metallic inclusion in the steel, is controlled at 0.01～0.02% in this steel.
P:P forms microsegregation when solidification of molten steel, gather partially at crystal boundary when austenitizing temperature heats subsequently, and the fragility of steel is enlarged markedly.The content of control P is below 0.030%, and content is low more good more.
S: can form FeS, come red brittleness to steel band.Control S content is below 0.030%, and content is low more good more.
Cr: one of carbide forming element in the rapid steel, mainly enter M23C6 in the annealed state, general content also plays an important role to the secondary hardening of steel about 4.0% in rapid steel.Therefore control its content 3.0～4.5%.
W, Mo: the main added elements in the rapid steel, main effect be form some amount be difficult to the dissolved primary carbide, make steel can carry out quench hot, and improve the wear resistance of steel near fusing point; Behind the martensite by the high temperature solid solution quenching high W of acquisition (Mo), M during tempering
2C and MC precipitation form the proeutectoid carbide of sufficient amount, are the principal elements of secondary hardening and red hardness.In steel of the present invention, control W content is 3.5～5.5%, and Mo content is 2.0～4.0%.
V: the main added elements in the rapid steel, V is to the disperse of the MC precipitate of the secondary hardening effect that plays that forms part and the link up conclusive effect that distributed.V content in general casting, the forging rapid steel forms MC type carbide between 1.0～3.0%, improve secondary hardness, red hardness and the wear resistance of steel.Be less than at 1.0% o'clock, the secondary hardness of steel, red hardness and wear resistance deficiency, being higher than 3.0% o'clock grindability can be poor.Therefore, V content is controlled at 0.80～1.5%.
Nb: the strong carbide forming element, form MC type carbide, can be used to part and substitute V or WO, V content is reduced to the level that only keeps secondary hardening.Utilize Nb to increase MC type carbide in the steel, thereby strengthen the wear resistance of rapid steel.But during the Nb too high levels, then shown the alligatoring to primary grain, carbide particle is thicker, and then rapid steel is difficult to grinding.Therefore, Nb content is controlled at 0.50～1.5%.
N:N adds as alloying element in rapid steel, because its atomic radius little (0.07nm), it in steel the gap solid solution element, effect is quite similar with C, form stable nitride with elements such as Al, Ti, Zr, V, can be dissolved in simultaneously among complicated M23C6, the M6C or MC, when quenching heating, also have small amount of nitrogen to enter in the matrix of steel by the solid solution of above carbide.But the eutectic net in the as-cast structure of minor N refinement rapid steel, refinement be (M6C) carbide once, but thereby refinement quenching autstenitic grain size; Allow high a little quenching temperature, thereby can increase age hardening effect and thermostability and hardness and flexible level of aggregation, can significantly improve cutting ability.The general normal N of the containing amount that electric arc furnace or induction furnace are smelted rapid steel adds 0.04～0.10% nitrogen content in the present invention by the method maintenance steel that adds nitrided ferro-chromium or V-N alloy at 0.02%..
The present invention has compared with prior art that cost is low, high yield, system easy to control the quality, be easy to scale operation, satisfies good secondary hardness and red hardness simultaneously, the advantage of impelling strength and bending strength application demand.Above-mentioned advantage is specific as follows: the secondary hardness difference 〉=65.2HRC of 540～600 ℃ of tempering (1160 ℃ of quenchings), 65.5HRC, 64.9HRC, 63.5HRC; 600～650 ℃ red hardness difference 〉=64HRC, 62.3HRC, 59HRC; The impelling strength difference 〉=53.3 of 580～600 ℃ of high temperings, 59.0Ak/Jcm
-2, 560～600 ℃ of tempered bending strength difference 〉=σ bb48180MPa, 5400MPa, 5287MPa.Reasonably the alloying proportioning has good comprehensive performances, saves alloy more than 20% than W9 steel, has better economic benefit.
The preparation method that the present invention is similar to prior art to employing:
Steel of the present invention can adopt electric arc furnace, high frequency furnace, vacuum induction furnace smelting, and molten steel casting becomes steel ingot, can carry out esr as required, through forging become a useful person or cogging after be rolled into rod, wire rod etc.
Embodiment
According to above-mentioned designed chemical ingredients scope, on the 25kg vacuum induction furnace, smelted 4 stoves steel of the present invention and 1 stove compared steel (W9), its concrete chemical ingredients is as shown in table 1.Molten steel casting becomes ingot, and makes φ 14mm, φ 18mm bar through forging.After the annealing of example steel and compared steel, be processed into sample, through quench, temper (1140～1220 ℃ of quenchings, 540～600 ℃ of tempering), its room-temperature mechanical property sees Table 2～7.
Steel of the present invention has the hardness higher than compared steel, red hardness, impelling strength and bending strength.
1. quench through uniform temp, after high temperature (540～600 ℃) tempering, the invention steel has the hardness higher than compared steel.(seeing Table 2,3,4)
2. after the quenching of uniform temp, temper, invention steel (3#, 4#) has than the better red hardness of compared steel, and anti-softening power is stronger.(seeing Table 5)
3. invention steel (3#, 4#) is through 1160 ℃ of quenchings, and when 580 ℃ of left and right sides tempering, impelling strength and bending strength are all above impelling strength and bending strength after the thermal treatment of compared steel (5#) normal temps.(seeing Table 6,7)
The chemical ingredients of table 1 embodiment and compared steel, weight %
Table 2 embodiment and 1140 ℃ of quenching differing tempss of compared steel tempered hardness value
Illustrate: (1) quenching test is carried out in air furnace, is incubated 10 minutes, oil quenching.
(2) the differing temps tempering is 3 times, is incubated 1 hour at every turn.
Table 3 embodiment and 1160 ℃ of quenching differing tempss of compared steel tempered hardness value
Illustrate: (1) quenching test is carried out in air furnace, is incubated 10 minutes, oil quenching.
(2) the differing temps tempering is 3 times, is incubated 1 hour at every turn.
Table 4 embodiment and 1200 ℃ of quenching differing tempss of compared steel tempered hardness value
Illustrate: (1) quenching test is carried out in air furnace, is incubated 10 minutes, oil quenching.
(2) the differing temps tempering is 3 times, is incubated 1 hour at every turn.
Table 5 embodiment and compared steel red hardness table
Table 6 embodiment and compared steel impact value table
Table 7 embodiment and compared steel bending strength value table
Claims (1)
1, a kind of high-performance low-alloy contains the Nb rapid steel, and it is characterized in that the concrete chemical ingredients composition of this rapid steel is by weight percentage: C 0.95～1.15%, and Si 0.20～0.40%, W 3.5～5.5%, Mo2.0～4.0%, Cr 3.0～4.5%, and V 0.80～1.5%, Nb 0.5～1.5%, RE 0.01～0.02%, S≤0.030%, P≤0.030%, Mn≤0.40%, all the other are Fe and unavoidable impurities.
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| Publication number | Priority date | Publication date | Assignee | Title |
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| CN101838774A (en) * | 2010-05-10 | 2010-09-22 | 金文平 | High speed steel and productive technology thereof |
| CN102259391B (en) * | 2011-07-21 | 2014-07-23 | 江苏华昌工具制造有限公司 | Soldering diamond saw blade |
| CN103290328A (en) * | 2013-05-30 | 2013-09-11 | 钢铁研究总院 | High-niobium, high-wear-resistance and high-toughness cold-work die steel |
| CN103643133A (en) * | 2013-11-29 | 2014-03-19 | 江苏精工特种材料有限公司 | Wear-resistant high-speed tool steel |
| CN103710636B (en) * | 2013-12-26 | 2016-03-16 | 山东省四方技术开发有限公司 | UOE welded tube joggling machine casting pressing mold and preparation method and foundry pattern |
| CN105886947A (en) * | 2016-04-18 | 2016-08-24 | 和县隆盛精密机械有限公司 | Abrasion-resistant taper-shank twist drill and preparation method thereof |
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| EP0105861A1 (en) * | 1982-09-14 | 1984-04-18 | Vereinigte Edelstahlwerke Aktiengesellschaft (Vew) | High speed steel alloy |
| US5435827A (en) * | 1991-08-07 | 1995-07-25 | Erasteel Kloster Aktiebolag | High speed steel manufactured by power metallurgy |
| CN1226609A (en) * | 1999-01-26 | 1999-08-25 | 尹道乐 | Economic high speed steel |
| CN1511969A (en) * | 2002-11-06 | 2004-07-14 | 大同特殊钢株式会社 | Alloy tool steel and its producing method and mold using it |
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- 2006-12-08 CN CNB2006101649433A patent/CN100469936C/en active Active
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0105861A1 (en) * | 1982-09-14 | 1984-04-18 | Vereinigte Edelstahlwerke Aktiengesellschaft (Vew) | High speed steel alloy |
| US5435827A (en) * | 1991-08-07 | 1995-07-25 | Erasteel Kloster Aktiebolag | High speed steel manufactured by power metallurgy |
| CN1226609A (en) * | 1999-01-26 | 1999-08-25 | 尹道乐 | Economic high speed steel |
| CN1511969A (en) * | 2002-11-06 | 2004-07-14 | 大同特殊钢株式会社 | Alloy tool steel and its producing method and mold using it |
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