EP0527276A1 - Abriebfester Stahl - Google Patents

Abriebfester Stahl Download PDF

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Publication number
EP0527276A1
EP0527276A1 EP91307390A EP91307390A EP0527276A1 EP 0527276 A1 EP0527276 A1 EP 0527276A1 EP 91307390 A EP91307390 A EP 91307390A EP 91307390 A EP91307390 A EP 91307390A EP 0527276 A1 EP0527276 A1 EP 0527276A1
Authority
EP
European Patent Office
Prior art keywords
steel
content
abrasion
resistance
abrasion resistant
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
Application number
EP91307390A
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English (en)
French (fr)
Other versions
EP0527276B1 (de
Inventor
Nobuo c/o Patent & License Dept. Shikanai
Tetsuya c/o Patent & License Dept. Sanpei
Kazunori c/o Patent & License Dept. Yako
Kenji c/o Patent & License Dept. Hirabe
Yasunobu c/o Patent & License Dept. Kunisada
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
JFE Engineering Corp
Original Assignee
NKK Corp
Nippon Kokan Ltd
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Application filed by NKK Corp, Nippon Kokan Ltd filed Critical NKK Corp
Priority to DE1991624234 priority Critical patent/DE69124234T2/de
Priority claimed from EP95120542A external-priority patent/EP0714990A1/de
Publication of EP0527276A1 publication Critical patent/EP0527276A1/de
Application granted granted Critical
Publication of EP0527276B1 publication Critical patent/EP0527276B1/de
Anticipated expiration legal-status Critical
Expired - Lifetime legal-status Critical Current

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    • 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
    • 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
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium

Definitions

  • the invention relates to the field of metallurgy and particularly relates to the field of an abrasion resistant steel utilized in the field of construction, civil engineering and mining.
  • Abrasion resistant steels are utilized in the field of construction, civil engineering and mining such as in power shovel, bulldozer, hopper and bucket to keep the lives of these machines or their parts. It is well known that the steel having high hardness possesses high abrasion resistance property. For this purpose a high alloyed steel treated by quenching has commonly been utilized.
  • Japanese Patent laid open Publication Nos. 142726/19 87, 169359/1988 and 142023/1989 disclose the information about the production of the conventional abrasion resistant steel.
  • the Brinell Hardness of the steel is more than 300.
  • the improvements are aimed at the weldability, the toughness and the workability in bending, and the abrasion resistance property is realized by increasing the hardness of the steel.
  • the property required for the abrasion resistant steel has recently become severer and the essential solution to higher abrasion resistance of steel will not be obtained by simply enhancing the hardness of steel.
  • the hardness of steel is significantly enhanced, the weldability and the workability of steel are deteriorated due to the high alloying and the cost of producing such steels increases significantly. Accordingly in the practical point of view the significant increase in the hardness of abrasion resistant steel is facing with a difficulty with respect to the workability of the steel.
  • an abrasion resistant steel having an excellent abrasion resistance property without considerably increasing the hardness of steel.
  • an abrasion resistant steel is provided with approximately 0.05 to 0.45 wt.% C, 0.1 to 1.0 wt.% Si, 0.1 to 2.0 wt.% Mn, 0.05 to 1.5 wt.% Ti and the balance Fe as the basic elements contributing to the enhancement of the abrasion resistance property.
  • At least one element selected from the group consisting of 0.1 to 2.0 wt.% Cu, 0.1 to 10.0 wt.% Ni, 0.1 to 3.0 wt.% Cr, 0.1 to 3.0 wt.% Mo and 0.0003 to 0.01 wt.% B may be added to enhance the quenching hardenability of the steel, and at least one element selected from the group consisting of 0.005 to 0.5 wt.% Nb, 0.01 to 0.5 wt.% V may be added to enhance the precipitation hardenability of the steel.
  • a more preferable range aiming at the economy of the steel is 0.05 to 0.3 wt.% in Ti content.
  • a more preferable range with respect to thr balance of the stable abrasion resistance and the economy of the steel is 0.3 to 1.0 wt.% in Ti content.
  • a more preferable range for stable abrasion resistance is 1.0 to 1.5 wt.% in Ti content.
  • a more preferable range aiming at the bending workability and the weldability of the steel is 0.05 to 0.2 wt.% in C content.
  • a more preferable range with respect to the balance of the bending workability and the weldability of the steel and the stable abrasion resistance of the steel is 0.2 to 0.35 wt.% in C content.
  • a more preferable range for stable abrasion resistance of the steel is 0.35 to 0.45 wt.% in C content.
  • Figure 1 is a graph showing the relationship between the added quantity of titanium and the ratio of resistance to abrasion.
  • the most significant characteristic of the invented steel is effectively utilizing of very hard TiC.
  • the purpose of the addition of titanium to steel is to react with the nitrogen so that the nitrogen is stabilized as TiN.
  • boron does not react with nitrogen since there is not enough nitrogen in the steel, and retained in the steel as a soluble boron, which enhances the quenching hardenability.
  • the quantity of the addition in this case is about 0.02 wt.% of steel.
  • the addition of a large quantity of titanium to steel is limited by the oxidation of the titanium in the steel melting stage, the clogging of the nozzle and the reaction with the oxidation preventing powder in the casting stage. Therefore the effect of the addition of a large quantity of titanium is not yet known.
  • Figure 1 is a graph showing the relationship between the added quantity of titanium and the ratio of resistance to abrasion.
  • the abscissa denotes the added quantity of titanium and the ordinate denotes the ratio of resistance to abrasion.
  • the ratio of resistance to abrasion is an index wherein the resistance to abrasion of an abrasion resistant steel is divided by that of a mild steel.
  • the resistance to abrasion is measured according to ASTM Standard G 65-85 wherein an abrasive is introduced between the test specimen and a rotating wheel with a chlorobutyl rubber tire.
  • the abrasive is a sand composed of 100% silica and of controlled size.
  • the C content of the test specimen is 0.3 wt.% and the specimen is heat treated by quenching.
  • the Brinell Hardness is below 500.
  • the ratio of resistance to abrasion linearly increases with the increase of the added quantity of titanium up to 0.5 wt.%.
  • the addition of titanium is effective when the added quantity of titanium is 0.05 wt.%. When the added quantity is 1.5 wt.%, the ratio of resistance to abrasion reaches about 10, which shows the remarkable improvement in the abrasion resistance property.
  • C is an indispensable element in forming TiC and also enhances the hardness of the matrix of steel. However when C is increased too much, the weldability and the workability are deteriorated. Therefore the upper limit of C is determined to be 0.45 wt.%. As for the lower limit of C the minimum quantity of C wherein the effect of TiC is shown is 0.05 wt.%.
  • a more preferable range aiming at the bending workability and the weldability of the steel is 0.05 to 0.2 wt.% in C content.
  • a more preferable range with respect to the balance of the bending workability and the weldability of the steel and the stable abrasion resistance of the steel is 0.2 to 0.35 wt.% in C content.
  • a more preferable range for the stable abrasion resistance of the steel is 0.35 to 0.45 wt.% in C content.
  • Si is an element effective in deoxidation process of steel making and a minimum addition of 0.1 wt.% is required for this purpose. Si is also an effective element for solution hardening. However when the Si content exceeds 1.0 wt.%, the toughness of steel is lowered and the inclusion in steel is increased. Therefore the Si content is determined to be 0.1 to 1.0 wt.%.
  • Mn is an element effective in quenching hardenability. At least 0.1 wt.% is required for this purpose. When the Mn content exceeds 2.0 wt.%, the weldability of steel is deteriorated. Therefore the Mn content is determined to be 0.1 to 2.0 wt.%.
  • Ti is one of the most important element as is C.
  • the addition of at least 0.05 wt.% of Ti is required to stably form a large quantity of TiC.
  • the Ti content exceeds 1.5 wt.%, the steel possesses good abrasion resistance property but high cost is required for the production, also the weldability and the workability of steel are lowered. Therefore the Ti content is required to be 0.05 to 1.5 wt.%.
  • a more preferable range aiming at the economy of the steel is 0.05 to 0.3 wt.% in Ti content.
  • a more preferable range with respect to the balance of the stable abrasion resistance and the economy of the steel is 0.3 to 1.0 wt.% in Ti content.
  • a more preferable range for stable abrasion resistance of the steel is 1.0 to 1.5 wt.% in Ti content.
  • At least one element selected from the group consisting of Cu, Ni, Cr, Mo and B may be added to enhance the quenching hardenability and at least one element selected from the group consisting of Nb and V may be added to enhance the precipitation hardening .
  • Cu is an element for enhancing the quenching hardenability and effective in controlling the hardness of steel.
  • the Cu content is below 0.1 wt.%, the effect is not sufficient.
  • the Cu content exceeds 2.0 wt.%, the hot workability is lowered and the production cost is increased. Therefore the Cu content is determined to be 0.1 to 2.0 wt.%.
  • Ni is an element which enhances the quenching hardenability and the low temperature toughness. When the Ni content is below 0.1 wt.%, the effect is not sufficient. When the Ni content exceeds 10.0 wt.%, the production cost is increased significantly. Therefore the Ni content is determined to be 0.1 to 10.0 wt.%.
  • Cr is an element which enhances the quenching hardenability.
  • the Cr content is below 0.1 wt.%, the effect is not sufficient.
  • the Cr content exceeds 3.0 wt.%, the weldability is deteriorated, and the production cost is increased. Therefore the Cr content is determined to be 0.1 to 3.0 wt.%.
  • Mo is an element which enhances the quenching hardenability. When the Mo content is below 0.1 wt.%, the effect is not sufficient. When the Mo content exceeds 3.0 wt.%, the weldability is deteriorated, and the production cost is increased. Therefore the Mo content is determined to be 0.1 to 3.0 wt.%.
  • B is an element which enhances the quenching hardenability by the addition to steel even by a small amount.
  • the B content is below 0.0003 wt.% , the effect is not sufficient.
  • the B content exceeds 0.01 wt.%, the weldability is deteriorated, and the quenching hardenability is also deteriorated. Therefore the B content is determined to be 0.0003 to 0.01 wt.%.
  • Nb is an element effective in the precipitation hardening and can control the hardness of steel according to the purpose of steel.
  • the Nb content is below 0.005 wt.%, the effect is not sufficient.
  • the Nb content exceeds 0.5 wt.%, the weldability is deteriorated. Therefore the Nb content is determined to be 0.005 to 0.5 wt.%.
  • V is an element effective in the precipitation hardening and can control the hardness of steel according to the purpose of steel.
  • the V content is below 0.01 wt.%, the effect is not sufficient.
  • the V content exceeds 0.5 wt.%, the weldability is deteriorated. Therefore the V content is determined to be 0.01 to 0.5 wt.%.
  • Table 1 shows the chemical compositions of the samples of the invented and conventional steel.
  • Samples from A to 0 are made of the invented steel, whereas samples from P to R are made of the steel for comparison.
  • the chemical composition of the samples from P to R varies with respect to Ti and other alloying elements.
  • the chemical compositions of the samples P and Q are within the same range with those of the invented steel except that of Ti.
  • the chemical composition of the sample R is within the same range of the invented steel with respect to Ti, but out of the range with respect to C.
  • Table 2 shows the process of making the samples, the ratio of the resistance to abrasion and the Brinell Hardness of the samples. Samples from A to O are made of the invented steel, whereas samples from P to R are made of the steel for comparison.
  • the abrasion test is carried out according to ASTM G 65-85 as described before.
  • the measurement of the abrasion is done by the change of the weight of the sample.
  • the ratio of resistance to abrasion is the ratio of the weight change of the specimen made of the invented steel versus that of the specimen made of a mild steel.
  • the processes in the table are classified as follows ; AR, as rolled; RQ, as quenched after heated to 900 °C following the rolling and air-cooling; RQT, as tempered at the temperature shown in the parenthesis after RQ treatment; DQ, as directly quenched after finish rolled at 880 °C following the heating of the slab at 1150 °C; DQT, as tempered at the temperature shown in the parenthesis following DQ.
  • the thickness of the sample is 15 mm.
  • the kind of steel in Table 1 corresponds with those in Table 2.
  • the steel for comparison P corresponds with the invented steel A, B-1 and D and the Ti content is below the range of the invented steel.
  • Examining the ratio of the resistance to abrasion it is found that the ratio is 4.9 in the steel for comparison P, whereas the ratio of the invented steel A is 6.5, that of the steel B-1, 8.3 and that of the steel D, 9.3. This is to say that the ratio of the invented steel can be enhanced twice as much as that of the steel for comparison which is a conventional abrasion resistant steel.
  • the hardness of the invented steel is lower than those of the steel for comparison.
  • the steel for comparison Q corresponds with the invented steel L and N.
  • the ratios of the resistance to abrasion in both L and N are higher than that of Q.
  • the steel for comparison R corresponds with the invented steel B-1.
  • the C content of the steel for comparison R is below the range of the invented steel. Since the C content of the steel R is so low that the ratio of the resistance to abrasion is significantly lower than that of B-1.
EP91307390A 1990-06-06 1991-08-12 Abriebfester Stahl Expired - Lifetime EP0527276B1 (de)

Priority Applications (1)

Application Number Priority Date Filing Date Title
DE1991624234 DE69124234T2 (de) 1991-08-12 1991-08-12 Abriebfester Stahl

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
JP2148399A JPH0441616A (ja) 1990-06-06 1990-06-06 低硬度で且つ耐摩耗性および曲げ加工性に優れた耐摩耗鋼の製造方法
JP14840090 1990-06-06
EP95120542A EP0714990A1 (de) 1990-06-06 1991-08-12 Verfahren zum Herstellen abriebfester Stähle

Publications (2)

Publication Number Publication Date
EP0527276A1 true EP0527276A1 (de) 1993-02-17
EP0527276B1 EP0527276B1 (de) 1997-01-15

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Family Applications (2)

Application Number Title Priority Date Filing Date
EP91307393A Expired - Lifetime EP0527277B1 (de) 1990-06-06 1991-08-12 Verfahren zur Herstellung abriebfester Stähle
EP91307390A Expired - Lifetime EP0527276B1 (de) 1990-06-06 1991-08-12 Abriebfester Stahl

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EP91307393A Expired - Lifetime EP0527277B1 (de) 1990-06-06 1991-08-12 Verfahren zur Herstellung abriebfester Stähle

Country Status (6)

Country Link
EP (2) EP0527277B1 (de)
JP (1) JPH0441616A (de)
AU (4) AU632187B2 (de)
CA (2) CA2033222A1 (de)
FI (2) FI101403B1 (de)
GB (2) GB2244718A (de)

Cited By (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2003062484A1 (en) * 2002-01-21 2003-07-31 Sandvik Ab Element for percussive rock drilling and method for its production
FR2847272A1 (fr) * 2002-11-19 2004-05-21 Usinor Procede pour fabriquer une tole en acier resistant a l'abrasion et tole obtenue
FR2847270A1 (fr) * 2002-11-19 2004-05-21 Usinor Procede pour fabriquer une tole en acier resistant a l'abrasion et tole obtenue
CN101880831A (zh) * 2010-06-13 2010-11-10 东北大学 一种高强度高韧性低合金耐磨钢及其制造方法
CN102851612A (zh) * 2011-06-29 2013-01-02 鞍钢股份有限公司 一种耐磨钢及其热处理方法
EP2657361A2 (de) * 2010-12-23 2013-10-30 Posco Stahlblech für ein öl/sand-aufschlämmungsrohr mit hervorragender abriebfestigkeit, korrosionsbeständigkeit und tieftemperaturbeständigkeit sowie herstellungsverfahren dafür
CN103556081A (zh) * 2013-10-30 2014-02-05 莱芜钢铁集团有限公司 一种高强高韧耐磨挖掘机斗齿用钢及其制造方法
EP2154262A4 (de) * 2007-05-29 2016-01-20 Jfe Steel Corp Abriebfestes stahlblech mit hervorragender verarbeitbarkeit und herstellungsverfahren dafür

Families Citing this family (12)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH0441616A (ja) * 1990-06-06 1992-02-12 Nkk Corp 低硬度で且つ耐摩耗性および曲げ加工性に優れた耐摩耗鋼の製造方法
US5236521A (en) * 1990-06-06 1993-08-17 Nkk Corporation Abrasion resistant steel
US5403410A (en) * 1990-06-06 1995-04-04 Nkk Corporation Abrasion-resistant steel
US5393358A (en) * 1990-12-03 1995-02-28 Nkk Corporation Method for producing abrasion-resistant steel having excellent surface property
JPH05239591A (ja) * 1992-02-27 1993-09-17 Nkk Corp 耐摩耗性に優れた鋼
US5292384A (en) * 1992-07-17 1994-03-08 Martin Marietta Energy Systems, Inc. Cr-W-V bainitic/ferritic steel with improved strength and toughness and method of making
US5409554A (en) * 1993-09-15 1995-04-25 The Timken Company Prevention of particle embrittlement in grain-refined, high-strength steels
US5827379A (en) * 1993-10-27 1998-10-27 Nippon Steel Corporation Process for producing extra high tensile steel having excellent stress corrosion cracking resistance
KR0153482B1 (ko) * 1994-08-16 1998-11-16 코오타니 토모카쭈 무한궤도용 링크의 제조방법
JP5017937B2 (ja) * 2005-12-28 2012-09-05 Ｊｆｅスチール株式会社 曲げ加工性に優れた耐摩耗鋼板
JP4899874B2 (ja) * 2007-01-12 2012-03-21 Ｊｆｅスチール株式会社 加工性に優れた耐摩耗鋼板およびその製造方法
CN105779885B (zh) * 2014-12-23 2018-03-27 上海梅山钢铁股份有限公司 一种具有良好加工性能的耐磨热轧薄钢板及其制造方法

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CH377540A (de) * 1956-02-06 1964-05-15 Rheinstahl Huettenwerke Ag Rad für Schienenfahrzeuge und Verfahren zu dessen Herstellung
GB982955A (en) * 1961-07-22 1965-02-10 Hoerder Huettenunion Ag The manufacture of articles or parts by cold-working steel
GB1060605A (en) * 1962-08-17 1967-03-08 Yawata Iron & Steel Co Welding filler metal
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DE1483210A1 (de) * 1965-11-23 1969-03-20 Hoerder Huettenunion Ag Verwendung eines unlegierten Stahls mit guter Abkantbarkeit in Laengs- und Querrichtung
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Cited By (17)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2003062484A1 (en) * 2002-01-21 2003-07-31 Sandvik Ab Element for percussive rock drilling and method for its production
FR2847272A1 (fr) * 2002-11-19 2004-05-21 Usinor Procede pour fabriquer une tole en acier resistant a l'abrasion et tole obtenue
FR2847270A1 (fr) * 2002-11-19 2004-05-21 Usinor Procede pour fabriquer une tole en acier resistant a l'abrasion et tole obtenue
WO2004048619A1 (fr) * 2002-11-19 2004-06-10 Industeel Creusot Procede pour fabriquer une tole en acier resistant a l'abrasion et tôle obtenue
WO2004048620A1 (fr) * 2002-11-19 2004-06-10 Industeel Creusot Procede pour fabriquer une tole en acier resistant a l'abrasion et tôle obtenue
US7459041B2 (en) 2002-11-19 2008-12-02 Industeel Creusot Method for making an abrasion-resistant steel plate
AU2003290188B2 (en) * 2002-11-19 2009-01-08 Industeel France Method for making an abrasion resistant steel plate and plate obtained
US7713362B2 (en) 2002-11-19 2010-05-11 Industeel Creusot Method for making an abrasion resistant steel plate and plate obtained
EP2154262A4 (de) * 2007-05-29 2016-01-20 Jfe Steel Corp Abriebfestes stahlblech mit hervorragender verarbeitbarkeit und herstellungsverfahren dafür
CN101880831A (zh) * 2010-06-13 2010-11-10 东北大学 一种高强度高韧性低合金耐磨钢及其制造方法
CN101880831B (zh) * 2010-06-13 2012-07-04 东北大学 一种高强度高韧性低合金耐磨钢的制造方法
EP2657361A2 (de) * 2010-12-23 2013-10-30 Posco Stahlblech für ein öl/sand-aufschlämmungsrohr mit hervorragender abriebfestigkeit, korrosionsbeständigkeit und tieftemperaturbeständigkeit sowie herstellungsverfahren dafür
EP2657361A4 (de) * 2010-12-23 2014-08-27 Posco Stahlblech für ein öl/sand-aufschlämmungsrohr mit hervorragender abriebfestigkeit, korrosionsbeständigkeit und tieftemperaturbeständigkeit sowie herstellungsverfahren dafür
US9238849B2 (en) 2010-12-23 2016-01-19 Posco Steel sheet for an oil sand slurry pipe having excellent abrasion resistance, corrosion resistance, and low-temperature toughness and method for manufacturing same
CN102851612A (zh) * 2011-06-29 2013-01-02 鞍钢股份有限公司 一种耐磨钢及其热处理方法
CN103556081A (zh) * 2013-10-30 2014-02-05 莱芜钢铁集团有限公司 一种高强高韧耐磨挖掘机斗齿用钢及其制造方法
CN103556081B (zh) * 2013-10-30 2015-12-30 莱芜钢铁集团有限公司 一种高强高韧耐磨挖掘机斗齿用钢及其制造方法

Also Published As

Publication number Publication date
AU3111293A (en) 1993-02-25
AU632187B2 (en) 1992-12-17
FI93863C (fi) 1995-06-12
GB2245282A (en) 1992-01-02
GB9027351D0 (en) 1991-02-06
FI101403B (fi) 1998-06-15
GB2244718A (en) 1991-12-11
GB9028005D0 (en) 1991-02-13
CA2033267C (en) 1999-08-24
FI906406A (fi) 1991-12-07
FI906406A0 (fi) 1990-12-27
CA2033222A1 (en) 1991-12-07
JPH0441616A (ja) 1992-02-12
EP0527276B1 (de) 1997-01-15
EP0527277A1 (de) 1993-02-17
FI93863B (fi) 1995-02-28
AU6783890A (en) 1991-12-12
FI906407A (fi) 1991-12-07
CA2033267A1 (en) 1991-12-07
FI101403B1 (fi) 1998-06-15
AU6772090A (en) 1991-12-12
AU1354595A (en) 1995-05-04
FI906407A0 (fi) 1990-12-27
EP0527277B1 (de) 1997-04-23

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