EP2134882A2 - Acier micro-allié à bonne tenue à l'hydrogène pour le formage à froid de pièces mécaniques à hautes caractéristiques - Google Patents
Acier micro-allié à bonne tenue à l'hydrogène pour le formage à froid de pièces mécaniques à hautes caractéristiquesInfo
- Publication number
- EP2134882A2 EP2134882A2 EP08787931A EP08787931A EP2134882A2 EP 2134882 A2 EP2134882 A2 EP 2134882A2 EP 08787931 A EP08787931 A EP 08787931A EP 08787931 A EP08787931 A EP 08787931A EP 2134882 A2 EP2134882 A2 EP 2134882A2
- Authority
- EP
- European Patent Office
- Prior art keywords
- steel
- hydrogen
- cold
- resistance
- molybdenum
- 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
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
Definitions
- the invention relates to micro-alloyed steels for the cold forming, particularly by striking, of assembly parts, such as screws, bolts, etc., which the automotive industry commonly uses for the assembly of the motor elements. or ground connections of rolling stock.
- Micro-alloy steel grades for screws with very high mechanical properties (1300 MPa and more resistance) have already been proposed to improve their resistance to hydrogen. This is the case, for example, of the grade described in USP 5,073,338 of December 1991 and in which molybdenum is added in an amount up to 1% by weight with a minimum of 0.5%.
- the object of the invention is to provide an economical micro-alloy steel, with a molybdenum content deliberately fixed for this purpose to less than 0.45% by weight, and having a good resistance to hydrogen, while achieving high mechanical characteristics on finished parts ready to use made from this steel.
- the subject of the invention is a micro-alloyed steel with good resistance to hydrogen embrittlement for the cold forming of mechanical parts with high characteristics, characterized in that, in order to contain its weight content of molybdenum below 0.45%, its chemical composition, in addition to iron and the inevitable residual impurities resulting from the elaboration of the steel, corresponds to the following analysis, given in percentages by weight: 0.3 ⁇ C% ⁇ 0 , 0.20 ⁇ Mo% ⁇ 0.45 0.4 ⁇ Mn% ⁇ l, 0 0.4 ⁇ Cr% ⁇ 2.0
- the subject of the invention is also a long rolled steel product (wire rod or rod) of micro-alloy steel resulting from continuous casting in the form of billets or blooms and having a chemical composition in accordance with the analysis given above. in order to be able to present, after processing by cold forming and quenching and tempering heat treatment, a mechanical strength of 1200 to 1500 MPa and more, combined with good resistance to hydrogen.
- the subject of the invention is also a ready-to-use mechanical part, formed cold, by striking in particular, and having high mechanical characteristics as well as good resistance to hydrogen, characterized in that it is microalloyed steel having the chemical composition given above and, preferably, produced from a long rolled steel product (bar or, more commonly, wire rod) from continuous casting in the form of billets or blooms.
- said mechanical part is an assembly screw for assembly in the automotive industry.
- a range of 0.20 to 0.45% Mo is in fact sufficient, in the case of the invention, to obtain a synergy between this particular element and the other elements present in the chemical composition of the polymer.
- these elements which are, on the one hand, niobium, vanadium and titanium (all of which act in the precipitated state in favor of a hardening of the grain of the steel structure and its refinement), and on the other hand, the boron present to increase the quenchability of the grade and which will ultimately result in a dominant martensite microstructure under the usual conditions of heat treatment specific to cold forming, by striking or otherwise.
- Hydrogen according to the invention, is therefore treated by the following three routes:
- the grade according to the invention has the particularity of multiplying and diversifying the hydrogen traps so as to avoid agglomeration in one place of carbides of the same type which would weaken the structure and adversely affect the mechanical strength of the steel. Molybdenum is no longer the preferred trap of hydrogen, since the grade also contains for this purpose niobium, titanium, chromium and vanadium.
- the elements such as boron, niobium, molybdenum, vanadium and titanium are favored because they allow to refine the grain, which increases the resistance to hydrogen. Indeed, the increase in grain fineness inducing an increase in the surface of the joints, the hydrogen is then better distributed in the steel and thus becomes less harmful.
- Hydrogen introduced into the steel during the preparatory phases of the material for the purpose of striking, may be partly eliminated during the final heat treatment of quenching and tempering performed on the struck pieces made of steel according to the invention.
- the increase of the temperature of income favors this degassing.
- This increase is made possible by the presence of hardening elements to go in this direction, such as vanadium, titanium, molybdenum, niobium, but also boron by its synergistic effect with niobium and molybdenum.
- the grade according to the invention makes it possible to achieve tempering temperatures of the order of 400 ° C. or more.
- the "ready-to-use" parts made with the steel grade according to the invention have in fact, without particular difficulties, a final ultimate strength of 1200 MPa, or even 1500 MPa (and even more, depending on the setting of the temperature that will be imposed for the final heat treatment), while initially displaying an intermediate resistance, at least half, or even a third only after a globularization annealing conducted preferentially just before the strike, for facilitate the work of this one
- molybdenum exhibits a strong interaction with phosphorus, limiting its harmful effect by limiting its segregation at the grain boundaries. In addition, it displays a marked carburigenic behavior. It allows, for given mechanical characteristics, higher temperatures of income, favoring suddenly the development of the carbides which will be traps with hydrogen. It is therefore an element that enhances the resistance to delayed fracture.
- manganese content tends, as a rule, to decrease the delayed fracture strength of the steel. This could be due to its interaction with sulfur leading to the formation of manganese sulphides. When we exceed thresholds of 1% of manganese, this interaction with sulfur could even lead to increase the fragility of steel with hydrogen, this, of course, in the absence of adequate provisions for the to avoid.
- manganese has a beneficial effect on the hardenability of steel and thus on the achievement of the final mechanical characteristics sought on the parts produced.
- the effect of phosphorus is particularly harmful in the steels according to the invention for several reasons.
- a contrarian effect of the hydrogen recombination it contributes to a higher concentration of atomic hydrogen likely to be able to penetrate into the material, thus to an increased risk of delayed rupture of the part in use.
- segregating at the grain boundaries it decreases their cohesion. Its content must therefore be kept very low. To this end, it will be ensured that the steel is dephosphorized when it is prepared in the liquid state.
- Silicon acts as deoxidizer of the steel during its elaboration, in the liquid state. Present in solid solution in solidified metal, it also increases the strength of steel. However, at too high a content (more than 0.2%), it can have a detrimental effect. During heat treatments, such as a globulization treatment, silicon tends to form intergranular oxides and thus reduces the cohesion of the grain boundaries. Too high a silicon content also decreases the ability of the steel to cold deformation by excessively hardening the matrix. It is mainly for this reason that, in the case of the steel grade according to the invention, its maximum content has been set at 0.2%.
- Aluminum is a deoxidizer of steel in the liquid state. It then contributes, in the form of nitrides, to control the magnification of the austenitic grain during hot rolling. On the other hand, present in too great a quantity, it can lead to a magnification of inclusions of aluminates type in the steel which can be detrimental to the properties of the metal, in particular its resilience.
- Chromium is generally sought for its hardening effect. Like molybdenum, it delays the softening of the income, allowing higher tempering temperatures which favors degassing but also the formation of carbides trapping hydrogen. At too high a content, by increasing the hardness of the steel excessively, it makes delicate its formatting by striking.
- This element provides an increase in the strength of the metal and has beneficial effects on the brittle fracture resistance. It also improves, in a well known manner, the resistance of steel to corrosion.
- niobium from 0.02 to 0.045% of niobium, from 0.03 to 0.30% of vanadium, and from 0.02 to 0.05% of titanium.
- These three elements are often added to the liquid steel to increase the hardness of the material.
- they will also increase the delayed breaking strength in several ways. They will help to refine the austenitic grain and form precipitates that trap hydrogen.
- niobium traps phosphorus.
- the hardening effect of each makes it possible to earn income at a higher temperature. Their maximum content is set here to avoid obtaining too large precipitates which would then be harmful vis-à-vis the resistance of the steel to delayed failure.
- niobium when added in excess, leads to an increased risk of "crack" defects on the surface of billets and continuous casting blooms. These defects, if they can not be completely eliminated, can be very detrimental to the respect of the integrity of the characteristics of the final part, in particular with regard to the resistance to fatigue and the resistance to hydrogen. This is the reason why, in the case of the grade according to the invention, its content had to be contained below 0.045%. 0.003 to 0.005% boron.
- boron By segregating with old austenitic grain boundaries, boron, even at very low levels, increases the hydrogen-induced delayed fracture strength. It greatly increases the hardenability of the steel and thus makes it possible to limit the carbon content necessary to obtain the desired martensitic microstructure. It increases the cohesion of the grain boundary by its intrinsic effect, but also by making it more difficult to segregate phosphorus at these grain boundaries. Finally, boron acts in synergy with molybdenum and niobium, thus increasing the efficiency of these elements and their own influences that allow their respective contents. An excess However, boron (above 0.005%) would lead to the formation of brittle iron boro-carbides.
- Sulfur is, for steel, a poison that expresses all its harmfulness in the presence of hydrogen, because it has an additive effect, that is to say, cooperative with it, forming in particular H 2 S, which in the middle wet in particular leads unstoppably to rapid physical degradation of parts. Its effect is in this respect much more marked than that of phosphorus. Its content must therefore be limited as far as possible, the closest to zero if possible, in any case not to exceed the limit of 0.015% enacted here. Steel must therefore be carefully desulphurized when it is prepared in the liquid state at the steelworks.
- Nitrogen is considered harmful. It traps boron by forming boron nitrides, which renders ineffective the role of this element on the hardenability of steel.
- TiN titanium nitride
- AlN aluminum nitride
- carbonitride precipitates which will help the trapping of hydrogen.
- This optimized composition makes it possible to have a very good resistance to hydrogen at the same time as a final mechanical strength of the steel, once transformed into a ready-to-use hammer after final heat treatment, greater than 1200 MPa and can even exceed 1,500 MPa, while retaining the same way as usual to carry out this transformation.
- the steel semi-finished product (bloom or, more generally, billet) is then hot-rolled in the austenitic range, according to the usual practice, until the a long rolled product, ready for shipment to customers after cooling to ambient.
- This long steel product is then in the form of bars, or more generally in the form of wire-wound machine for the selected applications.
- the wire-machine is then transformed into screw by cold stamping, schematically in the following conventional manner:
- the transformer receives the wire and after mechanical descaling (or chemical etching possibly followed by neutralization), it performs on the wire an annealing in a neutral atmosphere (under nitrogen for example).
- the yarn is then defatted before undergoing a first drawing, called drawing-roughing, for which a preliminary surface coating is provided, typically phosphating and soaping.
- drawing-roughing for which a preliminary surface coating is provided, typically phosphating and soaping.
- the diameter of the wire is reduced by about 30%.
- the wire-blank obtained is then subjected to a globulization treatment which, by providing a temporary drop in its hardness (intermediate Rm to about 500 MPa), will facilitate its subsequent forming, when striking, preserving the tool.
- This first heat treatment is followed by stripping, phosphating and soaping for a second drawing. This one is a finishing drawing, also called "final setting".
- the diameter reduction is more modest than before, generally less than 10%.
- the wire with a resistance temporarily weakened around 500 MPa, is then easily struck cold.
- the obtained raw stamping screws are first dephosphated, then subjected to a final quenching and tempering heat treatment, as well as to a final rolling operation to give the thread its final appearance.
- the rolling can be done either before the heat treatment or after.
- the income can advantageously operate at temperatures higher than the usual practice, namely of the order of 400 ° C and more, without compromising the achievement of the ultimate ultimate strength expected for screws produced ready. in use, with a Rm of 1200 to 1500 MPa and more .. Of course, the higher the income will be at high temperature, the lower the final Rm will be.
- the surface of the screws is then cleaned and coated with a layer of phosphates or, if appropriate, with any other suitable chemical or electrochemical coating.
- Castings A and 42CD4 are known steel shades of the prior art.
- Castings B, C and D are examples of the steel grade according to the invention.
- the known grade A comprises in particular a molybdenum content greater than 0.5% and the known grade 42CD4 does not contain niobium, vanadium, titanium or boron.
- the second column, Tr indicates the tempering temperature after quenching of the final pieces.
- the third column, Rm gives the tensile strength determined by pulling on standard specimens.
- the grades of the invention B, C and D make it possible to obtain hydrogen withstand and strength results equivalent to the known grade A containing more than 0.5% molybdenum.
- the known 42CD4 grade also containing little molybdenum, but containing no niobium, vanadium, boron or titanium, gives good results from a mechanical strength point of view, but does not offer a satisfactory performance at hydrogen.
- microalloyed steel according to the invention is therefore remarkable in that it exhibits both good aptitude for cold mechanical deformation (forging or forging) and good resistance to hydrogen (breaking strength). delayed) and in that it makes it possible to obtain, after tempering and tempering heat treatment, ready-to-use mechanical parts having a very high breaking strength.
- the steel grade of the invention is a raw material of choice for the industrial production of assembly parts with high mechanical properties required, such as screws for the automotive industry, when packaged in wire-machine or, more generally, in hot rolled long steel product resulting from continuous casting in the form of billets or blooms.
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Manufacturing & Machinery (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
- Heat Treatment Of Articles (AREA)
Abstract
Description
Claims
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
FR0702666A FR2914929B1 (fr) | 2007-04-12 | 2007-04-12 | Acier a bonne tenue a l'hydrogene pour le formage de pieces mecaniques a tres hautes caracteristiques. |
PCT/FR2008/000496 WO2008142275A2 (fr) | 2007-04-12 | 2008-04-09 | Acier micro-allié à bonne tenue à l'hydrogène pour le formage à froid de pièces mécaniques à hautes caractéristiques |
Publications (2)
Publication Number | Publication Date |
---|---|
EP2134882A2 true EP2134882A2 (fr) | 2009-12-23 |
EP2134882B1 EP2134882B1 (fr) | 2019-10-30 |
Family
ID=38521328
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP08787931.8A Active EP2134882B1 (fr) | 2007-04-12 | 2008-04-09 | Acier micro-allié à bonne tenue à l'hydrogène pour le formage à froid de pièces mécaniques à hautes caractéristiques |
Country Status (7)
Country | Link |
---|---|
US (1) | US9194018B2 (fr) |
EP (1) | EP2134882B1 (fr) |
JP (1) | JP5687898B2 (fr) |
KR (1) | KR20090128547A (fr) |
CN (1) | CN101688281B (fr) |
FR (1) | FR2914929B1 (fr) |
WO (1) | WO2008142275A2 (fr) |
Cited By (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2021009705A1 (fr) * | 2019-07-16 | 2021-01-21 | Arcelormittal | Procédé de production d'une pièce en acier, et pièce en acier |
Families Citing this family (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
KR101051241B1 (ko) * | 2010-08-30 | 2011-07-21 | 유니슨 주식회사 | 경도 균일성 및 기계적 강도가 우수한 금형강 제조 방법 |
EP2628807A1 (fr) | 2012-02-14 | 2013-08-21 | Swiss Steel AG | Elément de raccordement de type tige traité et son procédé de fabrication |
CN105401072B (zh) * | 2015-12-18 | 2018-01-02 | 马鞍山钢铁股份有限公司 | 含铌12.9级轨道交通移动装备用紧固件用钢及其热处理工艺 |
US12054817B1 (en) | 2020-11-10 | 2024-08-06 | United States Of America, Represented By The Secretary Of The Navy | High-strength and high-toughness austenitic steel |
EP4190934A1 (fr) | 2021-12-02 | 2023-06-07 | KAMAX Holding GmbH & Co. KG | Composant en acier allié b-zr |
Family Cites Families (9)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS61130456A (ja) * | 1984-11-29 | 1986-06-18 | Honda Motor Co Ltd | 高強度ボルト及びその製造方法 |
JP2614659B2 (ja) * | 1989-05-31 | 1997-05-28 | 株式会社神戸製鋼所 | 耐遅れ破壊性及び冷間鍛造性を備えた高強度ボルト用鋼 |
JPH11270531A (ja) * | 1998-03-19 | 1999-10-05 | Nippon Steel Corp | 遅れ破壊特性の優れた高強度ボルトおよびその製造方法 |
JP3718369B2 (ja) | 1999-05-13 | 2005-11-24 | 新日本製鐵株式会社 | 高強度ボルト用鋼及び高強度ボルトの製造方法 |
JP3857835B2 (ja) * | 1999-07-26 | 2006-12-13 | 新日本製鐵株式会社 | 高強度ボルト用鋼及び高強度ボルトの製造方法 |
JP4142853B2 (ja) * | 2001-03-22 | 2008-09-03 | 新日本製鐵株式会社 | 耐遅れ破壊特性に優れた高力ボルト |
JP3905332B2 (ja) * | 2001-07-10 | 2007-04-18 | 株式会社住友金属小倉 | 高強度ボルト用鋼 |
CN1266298C (zh) | 2004-09-14 | 2006-07-26 | 钢铁研究总院 | 耐延迟断裂和冷加工性能优良的高强度螺栓钢 |
JP4427012B2 (ja) * | 2005-07-22 | 2010-03-03 | 新日本製鐵株式会社 | 耐遅れ破壊特性に優れた高強度ボルトおよびその製造方法 |
-
2007
- 2007-04-12 FR FR0702666A patent/FR2914929B1/fr active Active
-
2008
- 2008-04-09 EP EP08787931.8A patent/EP2134882B1/fr active Active
- 2008-04-09 US US12/594,944 patent/US9194018B2/en active Active
- 2008-04-09 KR KR1020097023298A patent/KR20090128547A/ko not_active Application Discontinuation
- 2008-04-09 JP JP2010502546A patent/JP5687898B2/ja active Active
- 2008-04-09 WO PCT/FR2008/000496 patent/WO2008142275A2/fr active Application Filing
- 2008-04-09 CN CN2008800093066A patent/CN101688281B/zh active Active
Non-Patent Citations (1)
Title |
---|
See references of WO2008142275A2 * |
Cited By (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2021009705A1 (fr) * | 2019-07-16 | 2021-01-21 | Arcelormittal | Procédé de production d'une pièce en acier, et pièce en acier |
WO2021009543A1 (fr) * | 2019-07-16 | 2021-01-21 | Arcelormittal | Procédé de production de pièce en acier et pièce en acier |
Also Published As
Publication number | Publication date |
---|---|
JP2010523825A (ja) | 2010-07-15 |
FR2914929A1 (fr) | 2008-10-17 |
WO2008142275A2 (fr) | 2008-11-27 |
US9194018B2 (en) | 2015-11-24 |
CN101688281B (zh) | 2012-11-21 |
CN101688281A (zh) | 2010-03-31 |
US20100135745A1 (en) | 2010-06-03 |
KR20090128547A (ko) | 2009-12-15 |
EP2134882B1 (fr) | 2019-10-30 |
WO2008142275A4 (fr) | 2009-03-05 |
WO2008142275A8 (fr) | 2009-10-15 |
WO2008142275A3 (fr) | 2009-01-22 |
JP5687898B2 (ja) | 2015-03-25 |
FR2914929B1 (fr) | 2010-10-29 |
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