CN1092243C - Economic high speed steel - Google Patents
Economic high speed steel Download PDFInfo
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- CN1092243C CN1092243C CN99100266A CN99100266A CN1092243C CN 1092243 C CN1092243 C CN 1092243C CN 99100266 A CN99100266 A CN 99100266A CN 99100266 A CN99100266 A CN 99100266A CN 1092243 C CN1092243 C CN 1092243C
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Abstract
The present invention belongs to the field of steel alloy and is mainly suitable for manufacturing cutting tools, hot and cold moulds with high performance, machine components with abrasion resistance, etc. The present invention uses a plurality of carbide forming elements Cr in steel, so that expensive and rare elements, such as W, mo, etc., are saved. The present invention has the following chemical compositions: 0.70 to 1.20 wt% of C, 0.60 to 4.50 wt% of W, 0.60 to 4.00 wt% of Mo, 5.00 to 10.00 wt% of Cr, 0.60 to 1.50 wt% of V, 0.30 to 1.50 wt% of Si, 0.10 to 0.40 wt% of Mn, no more than 0.03 wt% of S, no more than 0.03 wt% of P, 10.010 to 1.20 wt% of A and Fe as the rest, wherein no more than 0.03 wt% of Ti, no more than 0.03 wt% of Nb and no more than 0.05 wt% of RE, wherein one or two kinds of the Ti, the Nb and the RE can be added. The present invention has the advantages of high hardness, red hardness, buckling strength, fine-quenched autstenitic grain size, high toughness and good plasticity.
Description
The invention belongs to field of alloy steel.Mainly be applicable to and make cutting tool, high-performance hot-cold die and the cold parts of wear-resisting machinery etc.
The main alloy element of rapid steel has W, Mo, V and Cr etc., and they all are carbide forming elements, under certain conditions, can both generate ledeburite in steel.In the steel that W is and W content is high, eutectic carbides mainly is M6C; In the steel that Mo is and Mo content is high, eutectic carbides mainly is M2C; In the high steel of V content, can generate the MC eutectic carbides; In the high steel of Cr content, have the M7C3 eutectic carbides and generate.Through after the hot-work, eutectic carbides is fractured into particulate state and is distributed in the steel, and these carbide are commonly referred to primary carbide.The existence of a large amount of carbide is key characters of rapid steel tissue, makes steel have higher hardness and wear resistance, and has guaranteed that the quenching autstenitic grain size of steel is thinner, therefore makes the toughness of steel better.
In existing all kinds of rapid steel, although the composition of elements such as W, Mo and V is change in the larger context all, but have only the composition change of Cr very little, about the content of Cr all is 4% in each rapid steel, therefore in existing rapid steel, find no existing based on the eutectic carbides M7C3 of Cr, only in the steel of as-annealed condition, just have based on the proeutectoid carbide M23C6 of Cr or M23C6 and M7C3 and from austenitic matrix, separate out.
W, Mo and V are expensive and rare element, the content of W and Mo all higher (content of V is also high in some steel) in rapid steel, so the cost height of rapid steel, price height.To use W and Mo in order saving, to reduce the cost of steel, invented some low-alloy high-speed steel kinds once, their common feature is that the content of W in the steel and Mo is reduced, and has added higher C and Si, to guarantee that steel still has higher hardness.But because W, Mo content reduce, the content of carbide forming element is reduced, thereby the carbide quantity in the steel is reduced, so the quenching autstenitic grain size chap of steel, the toughness of steel is descended, the use properties of steel has been produced adverse influence.This is the ubiquitous problem of low-alloy high-speed steel.
Cr is a carbide forming element, and the price of Cr is more much lower than W, Mo and V.Therefore imagination when the content of W in the steel and Mo reduces, if can suitably increase Cr content, can keep still that then more carbide forming element is arranged in the steel, thereby makes more alloy carbide is still arranged in the steel.So both reduced the cost of steel, and can make the autstenitic grain size of steel thinner again, toughness is better, and guarantees that steel still has higher hardness and wear resistance.
The possibility that adds higher Cr in steel exists, analyze its reason and mainly contain following 2 points: after 1. Cr content increases, to have M7C3 in the primary carbide of steel generates, and the hardness of M7C3 carbide is higher than M6C, the former is HV2300, the latter is 2060, therefore after part M7C3 carbide has substituted part M6C, still can keep the performance of steel.2. result of study recently shows, in the drawing process after rapid steel quenches, disperse is separated out from the quenched martensite matrix, can make among the carbide MC and M2C of steel generation secondary hardening, all contain more Cr, therefore explanation, Cr also has important contribution to the secondary hardening of rapid steel.According to above 2 reasons, adding more Cr in rapid steel is feasible with W and the Mo that substitutes part.Yet must be noted that following two problems: 1. the proportioning of elements such as the content of Cr and Cr and W, Mo and V should be suitable, accomplishes to reduce the cost of steel, can make the tissue and the better performances of steel again, meets the demands.2. select proper production process, particularly thermal treatment process, just can make steel obtain needed performance.
The patent No. provides the low-alloy high-speed steel of a kind of W of nothing for the Chinese patent of ZL93108767.8, and V content is higher, and after Overheating Treatment, this steel has higher hardness and red hardness.But this steel is Mo is steel, and oxidation and decarburizing tendency are serious; This steel Si content is low, and the M2C carbide is difficult for decomposing transformation, causes to have thick M2C angular particles in the steel, and is unfavorable to the performance of steel; Because the RE constituent content is too high, causes the inclusion in the steel more; Because the V content of this steel is higher, increased the cost of steel.
The purpose of this invention is to provide economic high speed steel, the cost of steel is significantly reduced, over-all properties is good, and particularly autstenitic grain size is thinner, and toughness is better.
According to purpose of the present invention, the main technical schemes that is adopted is the Cr content that suitably increases in the steel, reduce the content of elements such as W, Mo and V, adopt proper production process, make steel have higher hardness, red hardness and bending strength, the quenching autstenitic grain size is not less than 10 grades, and the toughness of steel is better, and cost obviously reduces.
The chemical ingredients scope of economic high speed steel of the present invention following (weight %):
C0.70-1.20, W0.60-4.50, Mo0.60-4.00, Cr5.00-10.00, V0.60-1.50, Si0.30-1.50, Mn0.10-0.40, S≤0.03, P≤0.03, Al0.01-1.20, all the other are Fe, can also add Ti≤0.3, Nb≤0.3, RE≤0.05, or in these back three kinds of elements two kinds or a kind of.
C is the fundamental element of rapid steel, and content is higher.C combines with elements such as W, Mo, Cr and V in the steel and generates alloy carbide, makes steel have good use propertieies such as higher hardness, red hardness and wear resistance.The height of C content is very big to the performance impact of steel, normally comes the carbon content of proportioning steel with reference to the balance carbon value.The carbon content of universal high speed steel is lower than balance carbon value, and the carbon content of some special high-speeds is suitable with the balance carbon value, and low-alloy high speed carbon content is generally all than balance carbon value height.
W and Mo are the strong carbide forming elements, are the main alloy element of rapid steel, and the secondary hardening of steel is played an important role, and be very big to the influences such as hardness, red hardness and wear resistance and grain fineness number of steel.The effect that it has been generally acknowledged that 1%Mo (weight) is equivalent to 1.4-2%W (weight) approximately.In the rapid steel that W is and W content is high, the as cast condition eutectic carbides mainly is M6C, and the primary carbide particle in steel also mainly is M6C.At WMo is in the steel, and the as cast condition eutectic carbides mainly is M2C, and it is metastable carbide, and in hot-work and heat treatment process, M2C decomposes, and is transformed into two kinds of carbide of M6C and a small amount of MC, so the primary carbide particle in the steel also mainly is M6C.In the high rapid steel of Mo system and Mo content, the as cast condition eutectic carbides mainly is M2C, and in hot-work and heat treatment process, M2C also takes place to decompose and changes, but change be difficult to carry out thorough, so in steel still residual some M2C particle.In the drawing process after quenching, the tiny M2C carbide of disperse is separated out from the quenched martensite matrix, keeps the coherence relation with matrix, and is very big to the secondary hardening contribution of steel, and no matter W system, WMo are or Mo is that the steel capital is like this.
V is the strong carbide forming element, can play an important role to the secondary hardening of steel, and is very big to the influence of hardness, wear resistance, thermotolerance and the grain fineness number etc. of steel.The primary carbide of V is MC, and its hardness is very high, is about 2840Hv.In the drawing process after quenching, the tiny MC carbide of disperse is separated out from the quenched martensite matrix with M2C, keeps the coherence relation with matrix, and is very big to the secondary hardening contribution of steel.
Cr is a carbide forming element, can improve hardening capacity, solidity to corrosion and the antioxidant property etc. of steel.In existing all kinds of rapid steel, the content of Cr all is about 4%, does not generally form the primary carbide based on Cr, but all contain a certain amount of Cr in primary carbides such as M6C, M2C and MC.In annealing process, have based on the proeutectoid carbide M23C6 of Cr or M23C6 and M7C3 and from austenitic matrix, separate out.In the drawing process after quenching, disperse is separated out from the quenched martensite matrix, keep among the carbide M2C and MC of coherence relation with matrix, all be dissolved with the Cr of some amount, this shows that Cr also has indirect important effect to the secondary hardening of rapid steel.When Cr content is higher, in the primary carbide of steel, have based on the carbide M7C3 of Cr and generate, this carbide hardness is higher than M6C, can both play a part good to hardness, wear resistance and the crystal grain thinning etc. of steel.
Nb and Ti are the strong carbide forming elements, can generate MC type carbide in steel, can crystal grain thinning, and increase wear resistance, but do not have the secondary hardening effect.When content is high in steel, can make the chap of MC carbide, Ti also easily generates inclusion, therefore should not use more.
RE can improve the thermoplasticity of steel, thereby can improve lumber recovery.But add-on should be suitable, too high add the affiliation inclusion is increased, unfavorable to the performance of steel.
Therefore Cr content among the present invention is 5-10%, than the Cr content height in the existing rapid steel, the M7C3 of some amount is arranged in the primary carbide of steel, to hardness, wear resistance and the crystal grain thinning of steel, improve toughness etc. and can play a part good.It is expensive and the content of rare element significantly descends the cost of steel suitably to have reduced the W in the steel, Mo and V etc.
The present invention has also added Al in right amount except C, W, Mo, Cr and V, Al can improve the thermotolerance and the toughness of steel.
The present invention has also added a certain amount of Si, with hardness that improves steel and the decomposition that promotes the M2C carbide.
The present invention can also add an amount of RE, and RE can improve the thermoplasticity of steel.
When containing element such as Nb, Ti in the steel scrap, can be used, make and contain suitable amount in the steel, they can form carbide refinement crystal grain, improve toughness, and the V content at this moment can corresponding minimizing steel is to reduce cost.
Production method of the present invention: can adopt electric arc furnace, induction furnace or electroslag furnace steel-making, be cast into steel ingot, forge, be rolled into bar or sheet material, be drawn into a material.The forging of steel, to roll temperature be 1100-1180 ℃, and final forging temperature is higher than 900 ℃, and the annealing temperature of finished steel is 750-870 ℃.Quenching temperature is 1020-1200 ℃, and tempering temperature is 500-540 ℃.
Steel produced according to the invention are quenched, tempered-hardness can reach HRC64-65, and 600 ℃ of red hardness can reach HRC55-57, and bending strength can reach 3600-4800Mpa.
Adopt steel of the present invention can produce cutting tools such as drill bit, milling cutter, broaching tool, screw tap, lathe tool and saw blade, mould and wear-resisting component of machine etc.
Compared with prior art, the present invention has following advantage:
1. owing to morely used the lower Cr element of price, thereby saved the expensive and consumption of rare element such as W, Mo and V, so the cost of steel is significantly reduced.
2. the quenching autstenitic grain size of steel is thinner, 〉=No10 level
3. the toughness of steel is better.
Embodiment
Guiding theory according to the present invention has designed the chemical ingredients of steel, has smelted 9 stove steel with induction furnace, and the chemical ingredients of 9 stove steel is listed in the table 1.Cast steel ingot after the smelting, be swaged into bar.The bar sampling of 9 stove steel is quenched and temper, measured hardness, red hardness and bending strength respectively, measuring result is listed in the table 2.Observation analysis the annealing of steel, quench and tempered structure.The annealing matrix of steel is the nodularization perlite.The quenching matrix is quenching Ma Huati, and the quenching autstenitic grain size is evenly thinner, and measuring result is listed in the table 3.The tempering matrix is a tempered martensite.Primary carbide particle in the steel has M6C, M7C3 and a small amount of MC.
Drill bit is processed in the employing wherein steel of two heat (batch) numbers, carries out cutting test.
(1) φ 8mm bit cutting test
Adopting embodiment heat (batch) number 1 prepared bar, be processed into the drill bit of φ 8mm, is 40Cr steel after modifier treatment by the material of drilling.The drill press spindle rotating speed: 940 rev/mins, cutting speed: 23.5 meters/minute, depth of cut: 22 millimeters, the amount of feed: 0.17 millimeter, the oil in water emulsion cooling, the boring number is 158.
(2) 8.6 millimeters bit cutting tests of φ
Adopt embodiment heat (batch) number 3 prepared bars, be processed into the drill bit of 8.6 millimeters of φ, be cut material and be the 40Cr steel after modifier treatment.The drill press spindle rotating speed: 940 rev/mins, cutting speed: 23.5 meters/minute, depth of cut: 22 millimeters, the amount of feed: 0.17 millimeter, the oil in water emulsion cooling, the boring number is 129.Table 1, the chemical ingredients of embodiment grade of steel (weight %)
| Heat (batch) number | Chemical component weight %) | |||||||||||||
| C | W | Mo | Cr | V | Si | Mn | S | P | Al | Ti | Nb | RE | Fe | |
| 1 | 0.90 | 1.08 | 2.02 | 6.01 | 1.02 | 1.03 | 0.36 | 0.026 | 0.029 | 0.01 | Surplus | |||
| 2 | 0.86 | 0.93 | 2.12 | 6.51 | 0.74 | 1.10 | 0.28 | 0.021 | 0.027 | 1.02 | 0.30 | 0.05 | Surplus | |
| 3 | 0.98 | 0.81 | 2.53 | 8.10 | 0.83 | 0.89 | 0.33 | 0.018 | 0.027 | 0.06 | Surplus | |||
| 4 | 0.88 | 0.94 | 2.24 | 9.18 | 0.60 | 1.13 | 0.26 | 0.025 | 0.023 | 0.95 | 0.29 | 0.27 | 0.04 | Surplus |
| 5 | 1.13 | 0.62 | 4.03 | 5.01 | 1.49 | 0.78 | 0.39 | 0.024 | 0.025 | 0.72 | 0.25 | Surplus | ||
| 6 | 1.12 | 1.18 | 3.46 | 7.45 | 1.23 | 1.09 | 0.12 | 0.019 | 0.028 | 1.18 | Surplus | |||
| 7 | 0.87 | 2.83 | 1.51 | 7.16 | 1.33 | 0.30 | 0.35 | 0.026 | 0.024 | 0.84 | Surplus | |||
| 8 | 0.70 | 4.49 | 0.61 | 8.58 | 0.74 | 1.27 | 0.29 | 0.025 | 0.028 | 0.03 | 0.31 | 0.05 | Surplus | |
| 9 | 1.20 | 1.12 | 1.04 | 10.01 | 1.42 | 1.50 | 0.23 | 0.022 | 0.028 | 1.10 | 0.03 | Surplus | ||
Hardness, red hardness and the bending strength of table 2 embodiment steel
The quenching autstenitic grain size of table 3 embodiment steel
| Heat (batch) number | Heat treating regime | Room temperature hardness HRC | 600 ℃ of red hardness HRC | Bending strength MPa | |
| Quenching temperature ℃ | Tempering temperature ℃ | ||||
| 1 | 1080 | 530 | 65 | 56 | 4300 |
| 2 | 1080 | 530 | 64 | 55 | 4500 |
| 3 | 1040 | 520 | 65 | 57 | 4100 |
| 4 | 1060 | 520 | 65 | 55 | 4300 |
| 5 | 1020 | 530 | 65 | 57 | 4000 |
| 6 | 1080 | 540 | 65 | 57 | 3900 |
| 7 | 1100 | 500 | 64 | 56 | 4600 |
| 8 | 1100 | 540 | 64 | 55 | 4800 |
| 9 | 1020 | 500 | 65 | 55 | 3600 |
| Heat (batch) number | Quenching temperature, ℃ | Autstenitic grain size, No |
| 1 | 1080 | 11-10 |
| 2 | 1080 | 11-12 |
| 3 | 1040 | 10-11 |
| 4 | 1060 | 11-12 |
| 5 | 1020 | 11-10 |
| 6 | 1080 | 11-10 |
| 7 | 1100 | 11-10 |
| 8 | 1100 | 11-12 |
| 9 | 1020 | 10-11 |
Claims (4)
1. economic high speed steel is characterized in that its chemical ingredients (weight %) is:
C0.70-1.20, W0.60-4.50, Mo0.60-4.00, Cr5.00-10.00, V0.60-1.50, Si0.30-1.50, Mn0.10-0.40, S≤0.03, P≤0.03, Al0.01-1.20, all the other are Fe.
2. in the economic high speed steel of claim 1, also can add a small amount of Ti, the content of Ti (weight %) is: Ti≤0.3.
3. in the economic high speed steel of claim 1 and claim 2, also can add small amount of N b, the content of Nb (weight %) is: Nb≤0.3.
4. in the economic high speed steel of claim 1, claim 2 and claim 3, also can add a small amount of rare earth elements RE, the content of RE (weight %) is: RE≤0.05.
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| Application Number | Priority Date | Filing Date | Title |
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| CN99100266A CN1092243C (en) | 1999-01-26 | 1999-01-26 | Economic high speed steel |
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| CN99100266A CN1092243C (en) | 1999-01-26 | 1999-01-26 | Economic high speed steel |
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| CN1092243C true CN1092243C (en) | 2002-10-09 |
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Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN100430510C (en) * | 2006-01-24 | 2008-11-05 | 江苏华久特钢工具有限公司 | High-performance low-cost high speed steel |
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| Publication number | Priority date | Publication date | Assignee | Title |
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| CN1168417A (en) * | 1997-02-04 | 1997-12-24 | 大连钢铁集团有限责任公司 | General purpose high-speed steel |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1168417A (en) * | 1997-02-04 | 1997-12-24 | 大连钢铁集团有限责任公司 | General purpose high-speed steel |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN100430510C (en) * | 2006-01-24 | 2008-11-05 | 江苏华久特钢工具有限公司 | High-performance low-cost high speed steel |
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