CN1038467A - High-strength and high ductility non-quenched and non-tempesed steel - Google Patents
High-strength and high ductility non-quenched and non-tempesed steel Download PDFInfo
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- CN1038467A CN1038467A CN 88103754 CN88103754A CN1038467A CN 1038467 A CN1038467 A CN 1038467A CN 88103754 CN88103754 CN 88103754 CN 88103754 A CN88103754 A CN 88103754A CN 1038467 A CN1038467 A CN 1038467A
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Abstract
The invention discloses tough non-hardened and tempered steel of a kind of high strength and complete processing thereof, belong to the low alloy steel technical field.Its moiety is: 0.30～0.42%C, 0.20～0.60%Si, 1.60～2.20%Mn,＜0.04%P,＜0.04%S, 0.02～0.14%V,＜0.1%Ti, 0.006～0.022%N, ≤ 0.030%Cr,＜0.10%AlS, all the other are iron and other unavoidable impurities.After the blank heating to 1200 ℃, promptly forge forging ratio＞5.The back naturally cooling is forged in final forging temperature＞1000 ℃.Non-hardened and tempered steel low temperature-20 of the present invention ℃ impact guarantee value＞30J/cm
2
Description
The invention belongs to the low alloy steel technical field.
As far back as in 1972 the forge hot non-hardened and tempered steel is just arranged in the world, though the intensity high tenacity is low, particularly low-temperature impact toughness is poor.Be used to make the non-hardened and tempered steel 49MnVS3 of automobile crane as West Germany at that time, tensile strength is about 850MPa, but ballistic work is only greater than 15J(DVM).In recent years, the gloomy special steel of West Germany's base of a fruit company (Thyssen Edelstahlwerke) proposed die forging bent axle 38MnSiVS6 by adjusting composition, and its composition is 0.38%C, 0.70%Si, and 1.35%Mn, 0.065%S, 0.10%V, tensile strength is 925MPa.In addition, also propose hot rolling and pay 44MnVS6 and the 42MnSiVS33 that does the wrist pin use, its composition is respectively 0.44%C, 0.70%Si, 1.45%Mn, 0.030%S, 0.12%V, and 0.42%C, 0.70%Si, 0.70%Mn, 0.25%S, 0.06%V, its tensile strength is respectively 1000MPa and 800MPa.More than have only 44MnVS6 to indicate the room temperature ballistic work in three kinds of steel to be about 28J(DVM) ,-20 ℃ ballistic work is 15～20J(DVM).
Japan's middle warm forging of invention in recent years makes non-hardened and tempered steel, and tensile strength is 940MPa, and the room temperature impact value is 99J/cm
2, its composition is 0.47%C, 0.23%Si, and 0.49%Mn, 0.012%P, 0.018%S, 0.049%Cr, 0.04%Ti, the Forge Heating temperature is 600 ℃, this temperature is unfavorable to the forging and the die forging of heavy parts.It is 785 ℃ that final forging temperature is also arranged, and tensile strength is 905MPa, and impact value is about 153J/cm
2Non-hardened and tempered steel, its composition is 0.40%C, 0.75%Mn, 0.06%Cr, 0.05%Nb.In addition, also having Heating temperature is 1050 ℃, and finishing temperature is 850 ℃, and tensile strength is 760MPa, and the room temperature impact value is 71J/cm
2The hot rolling non-hardened and tempered steel, its composition is 0.43%C, 0.27%Si, 0.77%Mn, 0.020%S, 0.78%Cr, 0.12%V, 0.05%Nb, 0.001%Ca.More than these steel grades all do not guarantee low temperature impact properties.
Domestic forge hot has 35MoVN with non-hardened and tempered steel, 40MnTi, and 40MnV, 45MnV, 45V etc. also have only the ballistic guarantee value of room temperature, do not have the guarantee value of low-temperature impact.
The present invention is directed to the problems referred to above, proposed low temperature-20 ℃ impact guarantee value greater than 30J/cm
2High-strength and high ductility non-quenched and non-tempesed steel, promptly non-hardened and tempered steel improves notched bar impact strength, particularly low-temperature impact toughness value when improving intensity.
The present invention presses quadrature L
12Table is smelted 12 stoves test steel on the 30KW25kg high frequency furnace, experimental factor has: C, Si, Mn, V, Ti, Cr, N.In addition, also smelt the test steel of each constituent content of a stove between high and low limit value, be used for verifying regression equation.The final forging temperature of 13 stoves test steel is without exception greater than 1000 ℃, and being swaged into the sample blank is the 22mm square rod, forges the back naturally cooling.
Draw with regression analysis:
1. C major control σ b, content should not reach requirement but surpass 0.42% impact property more than 0.3%.
2. Si does not have much influences to the room temperature impact value, but worsens low temperature impact properties, and Si is as the bioelement of reductor and reinforced ferrite in the steelmaking process.So Si content is 0.2～0.6% in the non-hardened and tempered steel of the present invention.
3. V does not have much influences to the room temperature impact value, but worsens low temperature impact properties, and than Si more so.And V is the bioelement that improves intensity as non-hardened and tempered steel of the present invention, and add-on is 0.02～0.14%, and when V content in the steel was 0.02%＜V＜0.06%, V, Ti must compound addings, and the total content of V, Ti should be greater than 0.07%.
4. Mn is when improving tensile strength, to the unique element that does not have infringement of low temperature impact properties, so non-hardened and tempered steel of the present invention is selected higher Mn content for use.
5. N impact toughness is harmful, but N generates VN in non-hardened and tempered steel of the present invention, the bioelement of TiN, and content was measured in the matrix too much because of it is solid-solubilized in above 0.022% o'clock, the influence of impact value is bigger, thus in the non-hardened and tempered steel of the present invention N content between 1.006～0.022%.
Draw from experimental result: reducing perlite percent by volume and refine austenite crystal grain, reduce separating out of ferrite network, is to improve the flexible method.In order to reach refine austenite crystal grain, thereby guarantee to obtain thinner ferrite crystal grain and pearlite colony, to improve the purpose of low-temperature flexibility, non-hardened and tempered steel of the present invention adopts:
1. VN that solid solubility temperature is high and TiN particle stop austenite crystal to be grown up;
2. bigger forging ratio;
3.1200 the Heating temperature about ℃;
4. shorten the soaking time after heating as far as possible.
The clear 61-264162 non-hardened and tempered steel contrast of non-hardened and tempered steel of the present invention and Japanese Patent, the present invention is:
1. improve manganese content, reduce even do not have chromium;
2. simplification production process;
3. the assurance of-20 ℃ of cold impact values is arranged.
The composition of non-hardened and tempered steel of the present invention is compared as following table with the composition of the clear 61-264162 non-hardened and tempered steel of Japanese Patent: (Wt%)
| Steel grade | C | Si | Mn | P | S |
| The present invention | 0.30～ 0.42 | 0.20～ 0.60 | 1.60～ 2.20 | <0.04 | <0.04 |
| Japanese Patent | 0.25～ 0.60 | 0.10～ 1.00 | 1.00～ 2.00 | 0.011～ 0.015 | 0.018～ 0.071 |
| Steel grade | V | Ti | N | Cr | Als (Al) |
| The present invention | ＊0.02～ 0.14 | ＊<0.1 | 0.006～ 0.022 | ≤0.030 | <0.10 |
| Japanese Patent | ** (<0.1) | 0.30～ 1.00 | Al0.031 ～0.037 |
*: when 0.02%＜V＜0.06%, V, Ti must compound addings, and V, Ti total content are greater than 0.07% simultaneously.
*: Ti content is not essential in the chemical ingredients of Japanese Patent non-hardened and tempered steel, and then content can not be above 0.1% if Ti is arranged.
The fabrication process condition of non-hardened and tempered steel of the present invention is compared with the fabrication process condition of the clear 61-264162 non-hardened and tempered steel of Japanese Patent, and the processing conditions of non-hardened and tempered steel of the present invention is good, and production process is simple.
Will carry out hot rolling or annealing or normalizing treatment before the warm forging of the clear 61-264162 non-hardened and tempered steel of Japanese Patent, it is few to reach before the warm forging ferrite content, the purpose that pearlite interlaminar spacing is little, and then be heated to 600～700 ℃ and carry out warm forging.Also to adopt big amount of finish for making steel can reach high strength.
Non-hardened and tempered steel of the present invention directly with blank heating to 1200 ℃, shortens soaking time as far as possible, requires forging ratio greater than 5 when forging, and final forging temperature is forged back naturally cooling (air cooling) greater than 1000 ℃.
The clear 61-264162 non-hardened and tempered steel of Japanese Patent does not have the impact guarantee value of low temperature-20 ℃.
Obviously, the clear 61-264162 non-hardened and tempered steel of Japanese Patent is heated to 600～700 ℃ and carries out warm forging processing, and processing conditions is abominable, requires to have very high forging level, require very big amount of finish to reach the purpose that improves intensity simultaneously again, this processing conditions is not suitable for the forging and the die forging of heavy parts.In addition, this non-hardened and tempered steel also will carry out hot rolling or annealing or normalizing treatment before warm forging.
This shows that the advantage of quenched and tempered steel of the present invention has:
1) chromium content is few even do not have, and meets the national conditions that China lacks chromium resource;
2) forging condition is good, and production process is simple, applicable to die forging, helps boosting productivity;
3) low temperature-20 ℃ impact value guarantees greater than 30J/cm
2
Embodiments of the invention are: smelt six stove steel on the 100KW110kg medium-frequency induction furnace, every stove steel waters into two steel ingots, each heavy 50kg, cogging became the 50mm square billet after each steel ingot was heated to 1250 ℃, be heated to 1200 ℃ then, promptly be swaged into the 22mm square rod, final forging temperature is all at 1000 ℃～1080 ℃.With the data of the clear 61-264162 non-hardened and tempered steel of Japanese Patent and the data of 40Cr quenched and tempered steel, 6 groups of data of data and non-hardened and tempered steel of the present invention as a comparison, from steel grades, processing conditions, comparing in aspects such as mechanical property, is listed as follows:
(table vides infra)
In the last table 1,2,3,4, the final forging temperature of 5, No. 6 non-hardened and tempered steels of the present invention is all greater than 1000 ℃.
*: the GB3077-82 data
*: " the steel alloy steel grade handbook first volumes certificate.Its treatment condition are: 870 ℃ of normalizings, 840 ℃ of 45 minutes oil quenchings, 550 ℃ of tempering 75 minutes, air cooling then.
The tensile strength of non-hardened and tempered steel embodiment more of the present invention is all greater than 900MPa from table;-20 ℃ impact value ak is all greater than 30J/cm
2; The room temperature impact property is also better.And the clear 61-264162 non-hardened and tempered steel of Japanese Patent is when Heating temperature is 600 ℃, and intensity is 958MPa, and when Heating temperature was elevated to 700 ℃, intensity just dropped to not enough 800MPa.
Claims (2)
1, a kind of high-strength and high ductility non-quenched and non-tempesed steel, it is characterized in that moiety (weight percent) is: 0.30～0.42%C, 0.20～0.60%Si, 1.60～2.20%Mn,＜0.04%P,＜0.04%S, 0.02～0.14%V,＜0.1Ti, 0.006～0.022%N, ≤ 0.030%Cr,＜0.10%Als ,] all the other are unavoidable impurities in iron and the steel.
2, a kind of high-strength and high ductility non-quenched and non-tempesed steel complete processing is characterized in that, blank heating to 1200 ℃ shortens soaking time as far as possible, forge, and forging ratio＞5, the back naturally cooling is forged in final forging temperature＞1000 ℃.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN 88103754 CN1038467A (en) | 1988-06-16 | 1988-06-16 | High-strength and high ductility non-quenched and non-tempesed steel |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN 88103754 CN1038467A (en) | 1988-06-16 | 1988-06-16 | High-strength and high ductility non-quenched and non-tempesed steel |
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| Publication Number | Publication Date |
|---|---|
| CN1038467A true CN1038467A (en) | 1990-01-03 |
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| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN 88103754 Granted CN1038467A (en) | 1988-06-16 | 1988-06-16 | High-strength and high ductility non-quenched and non-tempesed steel |
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| CN (1) | CN1038467A (en) |
Cited By (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1039835C (en) * | 1995-07-20 | 1998-09-16 | 张玉田 | Non-hardened and non-tempered alloy structure steel and making process thereof |
| CN100500918C (en) * | 2007-03-29 | 2009-06-17 | 攀钢集团成都钢铁有限责任公司 | Steel for large diameter non-tempering petroleum sleeve |
| CN102071368A (en) * | 2011-01-30 | 2011-05-25 | 钢铁研究总院 | Medium carbon non-quenched and tempered steel used in low-cost forging |
| CN103589970A (en) * | 2013-10-24 | 2014-02-19 | 南京钢铁股份有限公司 | Bar material for non-quenched and tempered shaft part and manufacturing process of bar material |
| CN104178613A (en) * | 2014-08-07 | 2014-12-03 | 山东金马工业集团股份有限公司 | Controllable cooling method for high-pressure common rail |
| CN104313449A (en) * | 2014-09-29 | 2015-01-28 | 中原特钢股份有限公司 | Production method of low-temperature high-strength high-toughness steel for lifting rings |
| CN109234627A (en) * | 2018-10-17 | 2019-01-18 | 南京钢铁股份有限公司 | A kind of high-strength and high-ductility Micro Alloying round steel and preparation method |
| CN109837461A (en) * | 2019-02-15 | 2019-06-04 | 江苏利淮钢铁有限公司 | A kind of the water jacket non-hardened and tempered steel and its manufacturing method of new-energy automobile |
| CN112143965A (en) * | 2019-06-28 | 2020-12-29 | 宝山钢铁股份有限公司 | Non-quenched and tempered oil casing pipe and manufacturing method thereof |
-
1988
- 1988-06-16 CN CN 88103754 patent/CN1038467A/en active Granted
Cited By (11)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1039835C (en) * | 1995-07-20 | 1998-09-16 | 张玉田 | Non-hardened and non-tempered alloy structure steel and making process thereof |
| CN100500918C (en) * | 2007-03-29 | 2009-06-17 | 攀钢集团成都钢铁有限责任公司 | Steel for large diameter non-tempering petroleum sleeve |
| CN102071368A (en) * | 2011-01-30 | 2011-05-25 | 钢铁研究总院 | Medium carbon non-quenched and tempered steel used in low-cost forging |
| CN103589970A (en) * | 2013-10-24 | 2014-02-19 | 南京钢铁股份有限公司 | Bar material for non-quenched and tempered shaft part and manufacturing process of bar material |
| CN103589970B (en) * | 2013-10-24 | 2016-03-30 | 南京钢铁股份有限公司 | The excellent Materials And Manufacturing Processes of Micro Alloying axial workpiece |
| CN104178613A (en) * | 2014-08-07 | 2014-12-03 | 山东金马工业集团股份有限公司 | Controllable cooling method for high-pressure common rail |
| CN104313449A (en) * | 2014-09-29 | 2015-01-28 | 中原特钢股份有限公司 | Production method of low-temperature high-strength high-toughness steel for lifting rings |
| CN109234627A (en) * | 2018-10-17 | 2019-01-18 | 南京钢铁股份有限公司 | A kind of high-strength and high-ductility Micro Alloying round steel and preparation method |
| CN109837461A (en) * | 2019-02-15 | 2019-06-04 | 江苏利淮钢铁有限公司 | A kind of the water jacket non-hardened and tempered steel and its manufacturing method of new-energy automobile |
| CN112143965A (en) * | 2019-06-28 | 2020-12-29 | 宝山钢铁股份有限公司 | Non-quenched and tempered oil casing pipe and manufacturing method thereof |
| CN112143965B (en) * | 2019-06-28 | 2022-06-28 | 宝山钢铁股份有限公司 | Non-quenched and tempered oil casing pipe and manufacturing method thereof |
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